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Citation: Yazdani, M.; Pot, C.;
Boyadjian, Q.; Liu, Y.; Yue, S.; Béland,
J.-F.; Bocher, P. Effect of
Unidirectional and Cross-Rolling on
the Texture Evolution of a Hot
Extruded AA6082. Eng. Proc. 2023,
43, 28. https://doi.org/10.3390/
engproc2023043028
Academic Editor: Houshang
Alamdari
Published: 18 September 2023
Copyright: © 2023 by the authors.
Licensee MDPI, Basel, Switzerland.
This article is an open access article
distributed under the terms and
conditions of the Creative Commons
Attribution (CC BY) license (https://
creativecommons.org/licenses/by/
4.0/).
Proceeding Paper
Effect of Unidirectional and Cross-Rolling on the Texture
Evolution of a Hot Extruded AA6082 †
Majid Yazdani 1,* , Clément Pot 1, Quentin Boyadjian 1, Yang Liu 2, Stephen Yue 2, Jean-François Béland 3
and Philippe Bocher 1
1Département de Génie Mécanique, École de Technologie Supérieure, 1100 Rue Notre-Dame Ouest,
Montréal, QC H3C 1K3, Canada; clement.pot.2@ens.etsmtl.ca (C.P.);
quentin.boyadjian.1@ens.etsmtl.ca (Q.B.); philippe.bocher@etsmtl.ca (P.B.)
2Materials Engineering Department, McGill University, Wong Building, 3610 University,
Montréal, QC H3A 0C5, Canada; yang.liu9@mail.mcgill.ca (Y.L.); steve.yue@mcgill.ca (S.Y.)
3
Conseil National de Recherches Canada, 501 Boulevard de l’UniversitéEst, Saguenay, QC G7H 8C3, Canada;
jean-francois.beland@cnrc-nrc.gc.ca
*Correspondence: majid.yazdaniesmaeilabad.1@ens.etsmtl.ca
†Presented at the 15th International Aluminium Conference, Québec, QC, Canada, 11–13 October 2023.
Abstract:
To illustrate how the texture evolution of a polycrystalline aluminum alloy is dependent
on the deformation path, hot extruded AA6082 plates in T6 conditions were rolled with various
deformation modes. Unidirectional and cross-rolling were conducted at room temperature for
different levels of thickness reduction. The resulting textures were then evaluated using the electron
backscatter diffraction technique. Depending on the extent of deformation, different textures were
obtained. The strong texture of the initial hot extruded material influences texture development
and provides new insights into texture development in aluminum alloys. The evolution of the Cube
component was particularly interesting in this matter. A competition between dislocation glide and
crystal rotation could explain the observed results. The comprehension of these mechanisms leads to
a better understanding of texture evolution that drives many properties in aluminum alloys.
Keywords: cold rolling; unidirectional rolling; cross-rolling; texture analysis; EBSD measurement; AA6082
1. Introduction
Aluminum alloys are the second most widely used metallic structural materials and
are used in the broadest range of products [
1
]. Their face-centred cubic (FCC) atomic
structure and their high stacking fault energy (SFE) exhibit a distinctive crystallographic
texture evolution during various stages of material processing [
2
]. Crystallographic texture,
which expresses the statistical distribution of grain orientations, plays a central role in the
performance of metals and alloys. Deformed and recrystallized aluminum alloys exhibit
distinct crystallographic textures that can generate different level of mechanical anisotropy
depending on the deformation level and recrystallization percentage [
3
,
4
]. One of the
deformation processes that is used to control deformation textures is the rolling process [
5
].
Rolling is a deformation process that involves applying compressive forces using
opposing rolls to decrease the thickness of a sample while keeping its width almost con-
stant (plane strain conditions) [
6
]. The reduction in thickness during cold rolling increases
the mechanical strength of the processed alloys. The higher the reduction, the higher the
dislocation density within the material, thereby increasing the stored energy that subse-
quently triggers recrystallization during heat treatment [
5
,
7
]. Previous studies [
5
,
8
,
9
] have
reported that Copper ({112} <111>), Brass ({110} <112 >), and S ({123} <634>) orientations are
prominent components of the plane strain rolling texture observed in polycrystalline alu-
minum. The deformation textures become stronger as the grains get elongated in the rolling
direction during deformation. Several factors, including the deformation path, rolling
Eng. Proc. 2023,43, 28. https://doi.org/10.3390/engproc2023043028 https://www.mdpi.com/journal/engproc
Eng. Proc. 2023,43, 28 2 of 9
geometry, friction, deformation temperature, initial grain size, shear banding, presence
of second-phase particles, and rolling reduction, impact the development of deformation
texture [5,8,9].
Several research studies offer significant contributions to the understanding of pro-
cessing parameters on the microstructure and texture properties of aluminum alloys.
Kumar et al. [7]
focused on the microstructure and texture evolution of AA3003 alloy
during different deformation processes, observing that the microstructure exhibited elon-
gated grains and a banded structure along the rolling direction as a result of cold rolling.
Cold rolling led to the formation of strong Brass, Copper, and S components while the Cube
orientation decreased. Studying the evolution of AA2195 alloy during T6 heat treatment
for samples process using different deformation paths, namely cross-rolling (CR) and unidi-
rectional rolling (UDR), Nayan et al. [
8
] found that the CR sample exhibited an initial Brass
texture, which later weakened after thermal treatment, whereas the UDR sample showed
an initial Copper texture that transformed into a Cube component after thermal treatment.
Chrominski and Lewandowska [
10
] conducted a study on the texture evolution of AA6082
alloy in the CR condition for the as-extruded sample. The initial fibrous texture transformed
into a random texture after a 50% reduction. Furthermore, with further reductions to 70%,
the texture evolution exhibited a different pattern, with a notable increase in the intensity
of the Brass component.
Despite numerous studies investigating the microstructure and texture evolution of
aluminum alloys under various deformation processes, there is a scarcity of information
concerning texture evolution under different deformation paths or rolling modes, particu-
larly for initial states in which the microstructure/texture has been stabilized by another
deformation process (here extrusion). Therefore, the present work reports the variations of
texture for different cold rolling reductions in UDR and CR of a hot extruded AA6082.
2. Materials and Methods
In this investigation, AA6082 in the T6 condition was used. It is an aluminum-
magnesium-silicon (Al-Mg-Si) alloy with composition details in Table 1. The material was
provided as an extruded rod with a diameter of 58 mm.
Table 1. Chemical composition of the tested alloys.
Alloy Mg Si Cu Mn Cr Fe Al
AA6082 0.64 0.85 0.01 0.39 0.13 0.16 Bal.
UDR and CR tests were performed to investigate the effects of thickness reductions
on the samples. The tests involved multiple passes with the average reduction being
2.5% per pass, resulting in thickness reductions of 20% and 60%. The initial sample
dimensions for UDR and CR experiments were 50
×
70
×
5 mm and 50
×
40
×
5 mm,
respectively. Cold rolling in the extrusion direction (ED) has a minimal effect on the texture
because the microstructure is already stable for elongation in this direction; the UDR tests
were performed perpendicular to the extrusion direction. This research outlines how the
crystallographic texture generated during extrusion gets destabilized by cold deformation
in the opposite direction. In CR, the samples underwent a 90
◦
rotation around the normal
direction (ND) between each 2.5% rolling pass. This rotation causes the transverse direction
(TD) of the previous rolling pass to become the new rolling direction (RD) for the current
pass. For the CR samples, the initial direction of the test was the same as that of the UDR
(perpendicular to the ED).
For examining texture and microstructure evolution under electron backscatter diffrac-
tion (EBSD) analysis, samples were cut from the center of the deformed metal and cold-
mounted. Figure 1illustrates the step-by-step process of acquiring orientation maps
through the EBSD test. The metallographic samples were cold-mounted using resin epoxy
and then ground using silicon carbide grinding paper with varying grades (240/480/600/
800/1200) to achieve a smooth surface. Ultrasound cleaners were employed to remove
Eng. Proc. 2023,43, 28 3 of 9
any debris remaining on the sample surfaces after grinding. The samples were further
polished using diamond particle solutions with particle sizes of 9, 3, and 1
µ
m. In order to
obtain an optimal surface quality for EBSD characterization and enhance the indexation,
vibrational polishing was conducted for 3 h using 0.05
µ
m diamond particle solutions. The
prepared specimens were subjected to EBSD testing using a Hitachi SU-70 field emission
gun scanning electron microscope. The analysis focused on the central area of the specimen,
with the RD positioned perpendicular to the surface, i.e., the EBSD testing was performed
on sections along the ND and TD. The ATEX software [
11
] was used to analyze the EBSD
data and generate various representations such as the EBSD map, Pole Figure (PF), and the
Inverse Pole Figure (IPF). Figure 1also displays the color code and the designated TD-ND
section used for all EBSD maps.
Eng. Proc. 2023, 43, 28 3 of 9
cold-mounted. Figure 1 illustrates the step-by-step process of acquiring orientation maps
through the EBSD test. The metallographic samples were cold-mounted using resin epoxy
and then ground using silicon carbide grinding paper with varying grades
(240/480/600/800/1200) to achieve a smooth surface. Ultrasound cleaners were employed
to remove any debris remaining on the sample surfaces after grinding. The samples were
further polished using diamond particle solutions with particle sizes of 9, 3, and 1 µm. In
order to obtain an optimal surface quality for EBSD characterization and enhance the in-
dexation, vibrational polishing was conducted for 3 h using 0.05 µm diamond particle
solutions. The prepared specimens were subjected to EBSD testing using a Hitachi SU-70
field emission gun scanning electron microscope. The analysis focused on the central area
of the specimen, with the RD positioned perpendicular to the surface, i.e., the EBSD testing
was performed on sections along the ND and TD. The ATEX software [11] was used to
analyze the EBSD data and generate various representations such as the EBSD map, Pole
Figure (PF), and the Inverse Pole Figure (IPF). Figure 1 also displays the color code and
the designated TD-ND section used for all EBSD maps.
Figure 1. Illustration of the process to acquire the results from the EBSD analysis.
3. Results
The as-received sample has a fibrous structure and exhibited a double fiber texture,
where the <001> and <111> orientations aligned parallel to the extrusion direction (TD
since the rolling direction is transverse to the extrusion direction), as illustrated in Figure
2 displaying the IPF and EBSD map of the as-received sample. The <001> fiber is repre-
sented by the red color, while the <111> fiber is depicted in blue. Figure 2 also provides
IPFs of the as-received sample. The IPFs confirm the findings obtained from the EBSD
map. The analysis reveals the presence of a two-fibrous texture, namely [111]||TD and
[001]||TD, with intensities of 13.66 and 5.5 multiples of random distribution (mrd) or ×R,
respectively. This indicates that the [111] and [001] crystallographic directions of many
grains align parallel to the transverse direction of the initial sample. Furthermore, a rela-
tively weaker orientation in [101]||RD with an intensity of 2.92 × R is observed before
rolling the samples.
Figure 1. Illustration of the process to acquire the results from the EBSD analysis.
3. Results
The as-received sample has a fibrous structure and exhibited a double fiber texture,
where the <001> and <111> orientations aligned parallel to the extrusion direction (TD
since the rolling direction is transverse to the extrusion direction), as illustrated in Figure 2
displaying the IPF and EBSD map of the as-received sample. The <001> fiber is represented
by the red color, while the <111> fiber is depicted in blue. Figure 2also provides IPFs of the
as-received sample. The IPFs confirm the findings obtained from the EBSD map. The anal-
ysis reveals the presence of a two-fibrous texture, namely [111]||TD and [001]||TD, with
intensities of 13.66 and 5.5 multiples of random distribution (mrd) or
×
R, respectively. This
indicates that the [111] and [001] crystallographic directions of many grains align parallel to
the transverse direction of the initial sample. Furthermore, a relatively weaker orientation
in [101]||RD with an intensity of 2.92 ×R is observed before rolling the samples.
In the UDR condition, upon rolling with a 20% reduction, there were no significant
changes observed in the microstructure, and the double fiber texture remained intact, as
depicted in Figure 3a. However, with a further increase in reduction up to 60%, the thick-
ness of the layers decreased, leading to the appearance of new color variations, indicating
deviations from the initial orientation (see Figure 3b). In certain regions, the red color
representing the <001> fiber faded, and new orientations increased. The IPFs also reveal a
decrease in the intensities of [111]||TD and [001]||TD orientations with increasing rolling
reductions, reaching values of 6.4
×
R and 2.21
×
R at a 60% reduction, respectively. Addi-
Eng. Proc. 2023,43, 28 4 of 9
tionally, it is evident that a new orientation emerged in the rolling direction ([111]||RD)
with increasing reductions [101]||RD orientations diminished as rolling is conducted in
the transverse direction.
Eng. Proc. 2023, 43, 28 4 of 9
Hot Extruded
Figure 2. EBSD map and IPF for the as-received material (hot extruded).
In the UDR condition, upon rolling with a 20% reduction, there were no significant
changes observed in the microstructure, and the double fiber texture remained intact, as
depicted in Figure 3a. However, with a further increase in reduction up to 60%, the thick-
ness of the layers decreased, leading to the appearance of new color variations, indicating
deviations from the initial orientation (see Figure 3b). In certain regions, the red color rep-
resenting the <001> fiber faded, and new orientations increased. The IPFs also reveal a
decrease in the intensities of [111]||TD and [001]||TD orientations with increasing rolling
reductions, reaching values of 6.4 × R and 2.21 × R at a 60% reduction, respectively. Addi-
tionally, it is evident that a new orientation emerged in the rolling direction ([111]||RD)
with increasing reductions [101]||RD orientations diminished as rolling is conducted in
the transverse direction.
(a) UDR–20%
(b) UDR–60%
Figure 3. EBSD map and IPF of UDR sample; (a) after 20% reduction, and (b) after 60% reduction.
In Figure 4, the changes in texture during cross-rolling of the as-received materials
are depicted using EBSD maps and IPF representations. In the EBSD maps, the colors used
to represent orientations in these images are aligned with TD (Figure 1) to track changes
in the initial fibers. As previously mentioned, the as-received material exhibits two dis-
tinct fibers, and their orientations remain relatively unchanged, with a 20% reduction. Af-
ter a 60% reduction (Figure 4b), the initial fiber axes can still be observed, although the
<111> fiber is relatively weakened compared to the as-received material. Figure 4 also dis-
plays the IPFs of cross-rolled samples. As the rolling reductions increase to 60%, the
Figure 2. EBSD map and IPF for the as-received material (hot extruded).
Eng. Proc. 2023, 43, 28 4 of 9
Hot Extruded
Figure 2. EBSD map and IPF for the as-received material (hot extruded).
In the UDR condition, upon rolling with a 20% reduction, there were no significant
changes observed in the microstructure, and the double fiber texture remained intact, as
depicted in Figure 3a. However, with a further increase in reduction up to 60%, the thick-
ness of the layers decreased, leading to the appearance of new color variations, indicating
deviations from the initial orientation (see Figure 3b). In certain regions, the red color rep-
resenting the <001> fiber faded, and new orientations increased. The IPFs also reveal a
decrease in the intensities of [111]||TD and [001]||TD orientations with increasing rolling
reductions, reaching values of 6.4 × R and 2.21 × R at a 60% reduction, respectively. Addi-
tionally, it is evident that a new orientation emerged in the rolling direction ([111]||RD)
with increasing reductions [101]||RD orientations diminished as rolling is conducted in
the transverse direction.
(a) UDR–20%
(b) UDR–60%
Figure 3. EBSD map and IPF of UDR sample; (a) after 20% reduction, and (b) after 60% reduction.
In Figure 4, the changes in texture during cross-rolling of the as-received materials
are depicted using EBSD maps and IPF representations. In the EBSD maps, the colors used
to represent orientations in these images are aligned with TD (Figure 1) to track changes
in the initial fibers. As previously mentioned, the as-received material exhibits two dis-
tinct fibers, and their orientations remain relatively unchanged, with a 20% reduction. Af-
ter a 60% reduction (Figure 4b), the initial fiber axes can still be observed, although the
<111> fiber is relatively weakened compared to the as-received material. Figure 4 also dis-
plays the IPFs of cross-rolled samples. As the rolling reductions increase to 60%, the
Figure 3. EBSD map and IPF of UDR sample; (a) after 20% reduction, and (b) after 60% reduction.
In Figure 4, the changes in texture during cross-rolling of the as-received materials are
depicted using EBSD maps and IPF representations. In the EBSD maps, the colors used to
represent orientations in these images are aligned with TD (Figure 1) to track changes in
the initial fibers. As previously mentioned, the as-received material exhibits two distinct
fibers, and their orientations remain relatively unchanged, with a 20% reduction. After a
60% reduction (Figure 4b), the initial fiber axes can still be observed, although the <111>
fiber is relatively weakened compared to the as-received material. Figure 4also displays
the IPFs of cross-rolled samples. As the rolling reductions increase to 60%, the previously
strong orientations of [111]||TD and [001]||TD show a weakening trend, resulting in
decreased intensities to the value of 5.34
×
R and 4.73
×
R, respectively. In contrast, a new
texture component, [111]||RD, emerges with an intensity of 2.15
×
R. Additionally, like
the UDR condition, the existing texture components of [101]||RD are eliminated.
Eng. Proc. 2023,43, 28 5 of 9
Eng. Proc. 2023, 43, 28 5 of 9
previously strong orientations of [111]||TD and [001]||TD show a weakening trend, re-
sulting in decreased intensities to the value of 5.34 × R and 4.73 × R, respectively. In con-
trast, a new texture component, [111]||RD, emerges with an intensity of 2.15 × R. Addi-
tionally, like the UDR condition, the existing texture components of [101]||RD are elimi-
nated.
(a) CR–20%
(b) CR–60%
Figure 4. EBSD map and IPF of CR sample: (a) after 20% reduction, and (b) after 60% reduction.
The results clearly indicate a significant change in texture evolution with increasing
reductions, as illustrated by the (111) PFs in Figure 5. The transition from an initially axi-
ally symmetric texture (Figure 5a) towards the Brass component becomes more evident in
the sample rolled with a 60% reduction for both conditions (Figure 5c,e). Table 2 presents
the texture components in different conditions, providing a clearer understanding of the
texture variation with increasing reductions. The analysis reveals that the Cube compo-
nent exhibits a maximum value in the as-received material. However, as the reductions
increase to 20%, the Cube component decreases, but it subsequently increases with further
reductions in both conditions at 60%. Alongside the Cube component, the Brass and S
components remain substantial in all conditions. On the other hand, the Goss and Copper
components exhibit negligible amounts across all conditions.
Table 2. Texture components in different conditions.
Component,
Symbol {hkl}<uvw> Conditions
As-Received UDR20 UDR60 CR20 CR60
Cube {001}<100> 17.45 5.25 10.58 7.25 10.17
Goss {011}<100> 0.04 0.04 1.31 0.046 0.2
Brass {011}<211> 56.02 63.92 63.38 62.89 69.09
S {123}<634> 26.42 30.69 23.18 29.69 20.23
Copper {112}<111> 0.006 0.029 0.8 0.044 0.05
Other 0.064 0.071 0.75 0.08 0.26
Figure 4. EBSD map and IPF of CR sample: (a) after 20% reduction, and (b) after 60% reduction.
The results clearly indicate a significant change in texture evolution with increasing
reductions, as illustrated by the (111) PFs in Figure 5. The transition from an initially axially
symmetric texture (Figure 5a) towards the Brass component becomes more evident in the
sample rolled with a 60% reduction for both conditions (Figure 5c,e). Table 2presents the
texture components in different conditions, providing a clearer understanding of the texture
variation with increasing reductions. The analysis reveals that the Cube component exhibits
a maximum value in the as-received material. However, as the reductions increase to 20%,
the Cube component decreases, but it subsequently increases with further reductions in
both conditions at 60%. Alongside the Cube component, the Brass and S components
remain substantial in all conditions. On the other hand, the Goss and Copper components
exhibit negligible amounts across all conditions.
Table 2. Texture components in different conditions.
Component,
Symbol {hkl}<uvw>
Conditions
As-Received UDR20 UDR60 CR20 CR60
Cube {001}<100> 17.45 5.25 10.58 7.25 10.17
Goss {011}<100> 0.04 0.04 1.31 0.046 0.2
Brass {011}<211−> 56.02 63.92 63.38 62.89 69.09
S{123}<634−> 26.42 30.69 23.18 29.69 20.23
Copper {112}<11−1−> 0.006 0.029 0.8 0.044 0.05
Other 0.064 0.071 0.75 0.08 0.26
Eng. Proc. 2023,43, 28 6 of 9
Eng. Proc. 2023, 43, 28 6 of 9
(a) As-received (b) UDR–20% (c) UDR–60%
(d) CR20 (e) CR60
(f) Main ideal crystal orientations
Figure 5. PFs in different conditions: (a) As-received condition, (b) UDR after 20% reduction, (c)
UDR after 60% reduction, (d) CR after 20% reduction, and (e) CR after 60%, and (f) Main ideal crystal
orientation.
4. Discussions
The as-received material, which corresponds to the hot extruded sample, exhibits a
fibrous structure that can be attributed to the characteristic nature of AA6082. This alloy
is well-known for its fibrous structure following the extrusion process. This fibrous struc-
ture is believed to be formed by the presence of numerous dispersoids in the alloy, which
effectively hinder the process of recrystallization during the extrusion process [12].
In addition, the initial material demonstrates a distinctive double fiber texture, with
the <001> and <111> orientations aligned parallel to the extrusion direction (Figure 2). This
characteristic fiber texture is commonly observed in non-recrystallized aluminum alloy
extruded profiles, as documented by various researchers [10,13]. In addition, the initial
orientations of the as-received material include the presence of Brass and S components,
which are part of the β-fiber. The β-fiber, consisting of the Brass, S, and Copper compo-
nents, is commonly observed in the deformation texture of FCC materials [13]. The as-
received material displays a strong Cube component in its texture, which is attributed to
the influence of plane strain compression. Additionally, the deformation process gave rise
to heterogeneities that contribute to the formation of Cube-oriented grains in FCC mate-
rials [14].
Figure 5.
PFs in different conditions: (
a
) As-received condition, (
b
) UDR after 20% reduction,
(c) UDR
after 60% reduction, (
d
) CR after 20% reduction, and (
e
) CR after 60%, and (
f
) Main ideal
crystal orientation.
4. Discussions
The as-received material, which corresponds to the hot extruded sample, exhibits a
fibrous structure that can be attributed to the characteristic nature of AA6082. This alloy is
well-known for its fibrous structure following the extrusion process. This fibrous structure
is believed to be formed by the presence of numerous dispersoids in the alloy, which
effectively hinder the process of recrystallization during the extrusion process [12].
In addition, the initial material demonstrates a distinctive double fiber texture, with
the <001> and <111> orientations aligned parallel to the extrusion direction (Figure 2).
This characteristic fiber texture is commonly observed in non-recrystallized aluminum
alloy extruded profiles, as documented by various researchers [
10
,
13
]. In addition, the
initial orientations of the as-received material include the presence of Brass and S com-
ponents, which are part of the
β
-fiber. The
β
-fiber, consisting of the Brass, S, and Copper
components, is commonly observed in the deformation texture of FCC materials [
13
]. The
as-received material displays a strong Cube component in its texture, which is attributed
to the influence of plane strain compression. Additionally, the deformation process gave
rise to heterogeneities that contribute to the formation of Cube-oriented grains in FCC
materials [14].
In the case of UDR, early stages of deformation result in dislocation activities that in-
duce grain rotation toward efficient slip activity. These combined mechanisms generate the
Eng. Proc. 2023,43, 28 7 of 9
expected texture components, particularly the dominant Brass and S orientations (Figure 5
and Table 2). Our findings align with previous studies conducted by Nayan et al. [
8
] and
Bhattacharjee et al. [
15
], which reported the presence of Brass and S orientations in the
rolled samples. However, in contrast to their findings, the amount of Copper orientation in
this study is negligible. Furthermore, even after undergoing a 60% reduction, the material
retained its fibrous structure along the extrusion direction. This can be attributed to the
fact that the initial material had a strong initial texture from the as-received state, which
made it resistant to significant changes even after substantial reductions. The reduced
presence of Cube components after a 20% reduction indicates that grain rotations have a
more pronounced effect under this condition. As the reduction is increased up to 60%, the
thickness of the regions belonging to the same fiber is reduced. The <001> fiber fades and
lead to the emergence of new orientation, i.e., color variations in the IPFs (Figure 3b). In
certain regions, the red color representing and gives way to new orientations, indicated
by the violet and yellow colors along TD. Furthermore, there is a notable decrease in the
amount of the Cube component at a 20% reduction, followed by an increase at higher
reduction levels (60%), although it remains lower than that of the as-received material. This
finding contradicts some previous studies, which reported a decrease in the amount of
Cube orientation with increasing rolling reduction. According to these studies, the Cube
component is considered metastable and undergoes conversion into the
β
fiber component
during cold rolling [16]. Previous studies have also observed that at rolling reductions up
to 63%, the initial Cube orientation is retained but exhibits a significant scatter in orienta-
tion [
17
]. In this study, the distinct behavior can be attributed to the strong initial texture,
which exhibits different characteristics compared to conventional behavior, necessitating
further analysis.
In the CR condition, it was observed that the changes in texture evolution align
with the changes observed in the UDR condition but with different kinetics. Previous
studies [8,10,18]
have reported that a change in the deformation path during the deforma-
tion process impacts the plastic behavior of metals, leading to the destabilization of the
dislocation substructure after each pass. In this study, it was observed that changing the
deformation path maintained the characteristics of the initial texture. The Brass component
increased in CR60 (69.09%) compared to the UDR condition (63.38%) as shown in Table 2.
Conversely, the S and Copper components exhibited a decrease from 23.18% and 0.8% in
UDR60 to 20.23% and 0.05% in CR60, respectively. These variations can be attributed to
the inherent nature of the CR process. The multiple changes in the rolling direction during
each pass activate different slip systems and induce multidirectional rotations, ultimately
altering the texture behavior of the processed material. In our investigation, it is worth
highlighting that although the Brass component exhibits the highest fraction among the
various components, the presence of significant amounts of S and Cube components is also
noteworthy. If the decrease in Cube orientation compared to the initial material after a
20% reduction, its reduction in intensity is less significant than for the UDR. With further
reduction, the Cube component increases more significantly than the UDR, although it
remained lower than the initial amount. Previous studies [
8
,
10
,
19
] examining different
materials such as cast and homogenized AA2195 alloy, as-extruded AA6082, and forged
and annealed electric copper samples have indicated that the Brass component is the
dominant component in the texture after cross-rolling. This could be attributed to the
fact that the previous studies concentrated mostly on higher levels of reduction, whereas
our reductions were comparatively lower. Therefore, it is conceivable to expect that with
increasing the reductions to higher levels in our research, the texture evolution will likely
exhibit a stronger alignment with the Brass component and become more pronounced.
5. Conclusions
This study investigated the texture evolution of as-received AA6082 under different
modes of cold rolling. The as-received material exhibited a fibrous structure, attributed
to the presence of dispersoids that impede recrystallization during extrusion. The texture
Eng. Proc. 2023,43, 28 8 of 9
evolution in both the cross-rolling (CR) and unidirectional rolling (UDR) conditions showed
similar changes, albeit with different kinetics. Despite undergoing a significant 60% reduc-
tion, the materials retained their fibrous structure along the extrusion direction due to the
strong initial texture. The deformation processes induced dislocation activities and grain
rotations, resulting in the dominant Brass and S orientations. The texture behavior was
influenced by the CR process, leading to an increase in the Brass component and a decrease
in the S and Copper components compared to UDR. Additionally, the Cube orientation
exhibited a lesser reduction in intensity during CR, indicating its greater stability under
this condition.
Author Contributions:
Conceptualization, C.P., M.Y., Q.B., P.B., Y.L. and S.Y.; methodology, C.P., M.Y.,
Q.B., J.-F.B., P.B., Y.L. and S.Y.; writing—review and editing, C.P., Q.B., M.Y. and P.B.; supervision, P.B.;
funding acquisition, P.B. All authors have read and agreed to the published version of the manuscript.
Funding:
The APC was funded by the National Research Council and Natural Sciences and Engi-
neering Research Council Canada.
Institutional Review Board Statement: Not applicable.
Informed Consent Statement: Not applicable.
Data Availability Statement:
No new data were created or analyzed in this study. Data sharing is
not applicable to this article.
Acknowledgments:
The authors are grateful to NRC Canada and Rio Tinto for their
technical support.
Conflicts of Interest: The authors declare no conflict of interest.
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