Effects of Sc and Zr on the texture and mechanical anisotropy of high strength Al - Zn - Mg alloy sheets
Texture, mechanical anisotropy and microstructure of aged Al–Zn–Mg, Al–Zn–Mg–0.1Sc–0.1Zr and Al–Zn–Mg–0.25Sc–0.1Zr (wt.%) alloy sheets were investigated by tensile tests and electron microscopy. Sc and Zr additions do not change the texture of homogenized and cold rolled alloys, but transfer the cub...
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Deng, Y. Yin, Z.M. Xu, G.F. Wang, Y.J. Lu, L.Y. Duan, J.Q. 2020-12-03T20:08:18Z 2020-12-03T20:08:18Z 2016 Effects of Sc and Zr on the texture and mechanical anisotropy of high strength Al - Zn - Mg alloy sheets / Y. Deng, Z.M. Yin, G.F. Xu, Y.J. Wang, L.Y. Lu, J.Q. Duan // Проблемы прочности. — 2016. — № 1. — С. 47-57. — Бібліогр.: 14 назв. — англ. 0556-171X https://nasplib.isofts.kiev.ua/handle/123456789/173416 539.4 Texture, mechanical anisotropy and microstructure of aged Al–Zn–Mg, Al–Zn–Mg–0.1Sc–0.1Zr and Al–Zn–Mg–0.25Sc–0.1Zr (wt.%) alloy sheets were investigated by tensile tests and electron microscopy. Sc and Zr additions do not change the texture of homogenized and cold rolled alloys, but transfer the cube texture of the aged Al–Zn–Mg alloy into -fiber rolling texture. With increasing Sc and Zr additions, the strength significantly increases, and mechanical anisotropy is enhanced. The strength is highest parallel to the rolling direction, whereas it is lowest at a 45° angle to the rolling direction. The higher strength is mainly due to grain boundary strengthening and precipitation strengthening caused by Al₃ScxZr₁₋x nano-particles. The stronger mechanical anisotropy is ascribed to the rolling texture, due to the inhibitory effect of Al₃ScxZr₁₋x on recrystallization. A new model was successfully established to reveal the interrelation between Sc and Zr additions, texture and yield strength anisotropy of Al–Zn–Mg sheets. en Інститут проблем міцності ім. Г.С. Писаренко НАН України Проблемы прочности Научно-технический раздел Effects of Sc and Zr on the texture and mechanical anisotropy of high strength Al - Zn - Mg alloy sheets Влияние добавок Sc и Zr на текстуру и механическую анизотропию листов из высокопрочного сплава Al-Zn-Mg Article published earlier |
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Digital Library of Periodicals of National Academy of Sciences of Ukraine |
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Effects of Sc and Zr on the texture and mechanical anisotropy of high strength Al - Zn - Mg alloy sheets |
| spellingShingle |
Effects of Sc and Zr on the texture and mechanical anisotropy of high strength Al - Zn - Mg alloy sheets Deng, Y. Yin, Z.M. Xu, G.F. Wang, Y.J. Lu, L.Y. Duan, J.Q. Научно-технический раздел |
| title_short |
Effects of Sc and Zr on the texture and mechanical anisotropy of high strength Al - Zn - Mg alloy sheets |
| title_full |
Effects of Sc and Zr on the texture and mechanical anisotropy of high strength Al - Zn - Mg alloy sheets |
| title_fullStr |
Effects of Sc and Zr on the texture and mechanical anisotropy of high strength Al - Zn - Mg alloy sheets |
| title_full_unstemmed |
Effects of Sc and Zr on the texture and mechanical anisotropy of high strength Al - Zn - Mg alloy sheets |
| title_sort |
effects of sc and zr on the texture and mechanical anisotropy of high strength al - zn - mg alloy sheets |
| author |
Deng, Y. Yin, Z.M. Xu, G.F. Wang, Y.J. Lu, L.Y. Duan, J.Q. |
| author_facet |
Deng, Y. Yin, Z.M. Xu, G.F. Wang, Y.J. Lu, L.Y. Duan, J.Q. |
| topic |
Научно-технический раздел |
| topic_facet |
Научно-технический раздел |
| publishDate |
2016 |
| language |
English |
| container_title |
Проблемы прочности |
| publisher |
Інститут проблем міцності ім. Г.С. Писаренко НАН України |
| format |
Article |
| title_alt |
Влияние добавок Sc и Zr на текстуру и механическую анизотропию листов из высокопрочного сплава Al-Zn-Mg |
| description |
Texture, mechanical anisotropy and microstructure of aged Al–Zn–Mg, Al–Zn–Mg–0.1Sc–0.1Zr and Al–Zn–Mg–0.25Sc–0.1Zr (wt.%) alloy sheets were investigated by tensile tests and electron microscopy. Sc and Zr additions do not change the texture of homogenized and cold rolled alloys, but transfer the cube texture of the aged Al–Zn–Mg alloy into -fiber rolling texture. With increasing Sc and Zr additions, the strength significantly increases, and mechanical anisotropy is enhanced. The strength is highest parallel to the rolling direction, whereas it is lowest at a 45° angle to the rolling direction. The higher strength is mainly due to grain boundary strengthening and precipitation strengthening caused by Al₃ScxZr₁₋x nano-particles. The stronger mechanical anisotropy is ascribed to the rolling texture, due to the inhibitory effect of Al₃ScxZr₁₋x on recrystallization. A new model was successfully established to reveal the interrelation between Sc and Zr additions, texture and yield strength anisotropy of Al–Zn–Mg sheets.
|
| issn |
0556-171X |
| url |
https://nasplib.isofts.kiev.ua/handle/123456789/173416 |
| citation_txt |
Effects of Sc and Zr on the texture and mechanical anisotropy of high strength Al - Zn - Mg alloy sheets / Y. Deng, Z.M. Yin, G.F. Xu, Y.J. Wang, L.Y. Lu, J.Q. Duan // Проблемы прочности. — 2016. — № 1. — С. 47-57. — Бібліогр.: 14 назв. — англ. |
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2025-11-24T19:06:50Z |
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2025-11-24T19:06:50Z |
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| fulltext |
UDC 539.4
Effects of Sc and Zr on the Texture and Mechanical Anisotropy of High
Strength Al–Zn–Mg Alloy Sheets
Y. Deng,
a,1
Z. M. Yin,
a
G. F. Xu,
a
Y. J. Wang,
b
L. Y. Lu,
b
and J. Q. Duan
b
a School of Materials Science and Engineering, Central South University, Hunan, Changsha, China
b Northeast Light Alloy Co. Ltd, Hei Longjiang, Harbin, China
1 csudengying@163.com
Texture, mechanical anisotropy and microstructure of aged Al–Zn–Mg, Al–Zn–Mg–0.1Sc–0.1Zr and
Al–Zn–Mg–0.25Sc–0.1Zr (wt.%) alloy sheets were investigated by tensile tests and electron
microscopy. Sc and Zr additions do not change the texture of homogenized and cold rolled alloys, but
transfer the cube texture of the aged Al–Zn–Mg alloy into �-fiber rolling texture. With increasing Sc
and Zr additions, the strength significantly increases, and mechanical anisotropy is enhanced. The
strength is highest parallel to the rolling direction, whereas it is lowest at a 45� angle to the rolling
direction. The higher strength is mainly due to grain boundary strengthening and precipitation
strengthening caused by Al3ScxZr1-x nano-particles. The stronger mechanical anisotropy is ascribed
to the rolling texture, due to the inhibitory effect of Al3ScxZr1–x on recrystallization. A new model was
successfully established to reveal the interrelation between Sc and Zr additions, texture and yield
strength anisotropy of Al–Zn–Mg sheets.
Keywords: metals, mechanical anisotropy, microstructure, tensile test, electron backscatter
diffraction (EBSD), transmission electron microscopy (TEM), X-ray diffraction (XRD).
Introduction. For aerospace high-strength Al–Zn–Mg alloy to achieve suitable
mechanical properties, hot or cold deformation and heat treatment are inevitable, which can
give rise to the development of a characteristic texture, leading to mechanical anisotropy of
the final sheet products [1, 2]. The mechanical anisotropy plays a vital role in the fracture
and deformation and limits the engineering applications of alloy sheets. During engineering
design, only the poorest property values of the plates can be used as a design basis, and high
in-plane anisotropy increases the difficulty in forming. Therefore, it is of great importance
to investigate the mechanical property of alloy plates, especially for the new alloys [3].
Compared with traditional Al–Zn–Mg alloys, new Al–Zn–Mg–Sc–Zr alloys exhibit a
higher strength, excellent corrosion resistance and better weldability, which can be ascribed
to the formation of extremely fine and coherent Al3ScxZr1–x nano-particles [4–6]. However,
Bate [7] and co-authors indicate that when fine particles generating Zener pinning forces on
grain boundaries are present, a “brass” texture develops during deformation. Furthermore,
our previous work [8] reveals that the Sc and Zr can change the recrystallization texture
from cubic texture to �-fiber rolling texture and transfer the recrystallization nucleation
mechanism from cubic nucleation to high stored energy nucleation during static annealing.
However, there are no reports attempting to correlate Sc and Zr additions (fine Al3ScxZr1–x
particles), texture, mechanical anisotropy and microstructure in aluminum alloys, which
highly limits the engineering application of new Al–Zn–Mg–Sc–Zr alloy.
In this paper, we aim to investigate the effect of Sc and Zr microalloying additions on
texture, mechanical anisotropy and microstructure of Al–Zn–Mg alloy sheets and try to
construct a model to reveal their interrelation mechanism.
1. Experimental. 2-mm thick aged Al–5.65Zn–2.0Mg, Al–5.69Zn–1.98Mg–0.1Sc–
0.1Zr and Al–5.7Zn–1.98Mg–0.25Sc–0.1Zr (wt.%) alloy sheets were provided by Northeast
Light Alloy Co. Ltd. The detailed thermo-mechanical history of aged sheets was reported in
our previous work [9].
© Y. DENG, Z. M. YIN, G. F. XU, Y. J. WANG, L. Y. LU, J. Q. DUAN, 2016
ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2016, ¹ 1 47
To evaluate the in-plane mechanical anisotropy of the T6 sheets, the tensile specimens
were sectioned in different orientation angles between the tensile direction and the rolling
direction in rolling surface, as shown in Fig. 1. In this study, the deviation angles were set
as 0, 30, 45, 60, and 90�. The mechanical properties of all studied alloys were evaluated by
room temperature tensile tests on CSS-44100 tensile tester, which were carried out at a
cross-head speed of 2 mm/min, using different oriented tensile specimens with a gauge
length of 60 mm and a width of 15 mm.
Macrotexture measurements using standard XRD were performed on the mid-thickness
rolling plane (the plane containing the rolling and transverse directions) of the specimens.
EBSD analyses were performed to observe the microtexture, utilizing a Sirion 200 field
emission gun scanning electron microscope equipped with EBSD system. The detailed
methods for XRD and EBSD measurements were the same as our previous paper [8].
2. Results and Discussion.
2.1. Effect of Sc and Zr on In-Plane Mechanical Anisotropy of Aged Alloy Sheets.
The index of in-plane anisotropy (IPA) factor of three aged alloy sheets can be calculated
according to the following equation:
IPA
N X X X X X
N
mid mid mid N
�
� � � � � �
�
�[( ) ... ]
(
max ( ) min1
1
1 2 2
)
%,
maxX
�100 (1)
where N is the number of sampling directions, X max and X min are the maximum and
minimum values, respectively, for mechanical properties, such as elongation (EI), ultimate
tensile strength (UTS), and yield strength (YS). In this study, the sectioning directions
deviate from rolling direction, and the deviation angle are 0, 30, 45, 60, and 90�, and thus
N is equal to 5.
Figure 2 and Table 1 show the mechanical properties of three alloys and their
corresponding in-plane anisotropy indexes. As seen from Fig. 2, the strength is highest and
the elongation is lowest when the tensile axis is parallel to rolling direction. Moreover, the
ultimate tensile strength and yield strength of three alloys all reach their minimum values
when the deviation angle is 45�. It can be found that with the increase of Sc additions the
mechanical anisotropy of strength and elongation gradually increases.
Y. Deng, Z. M. Yin, G. F. Xu, et al.
48 ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2016, ¹ 1
Fig. 1. The position of tensile specimens to mechanical properties.
T a b l e 1
IPA Values of Mechanical Properties (%)
Alloy YS UTS EI
Al–Zn–Mg 1.7 1.1 6.00
Al–Zn–Mg–0.1Sc–0.1Zr 5.0 8.0 17.19
Al–Zn–Mg–0.25Sc–0.1Zr 7.2 8.2 18.08
2.2. Macrotexture Evolution during the Preparation of Alloy Sheets. Figure 3 shows
the X-ray macrotextures of three alloys in homogenized, cold rolled and aged states.
Figure 3a–c shows there is no obvious preferred orientation in homogenized alloys, except
for weak {100} fiber texture. After cold rolling, �-fiber texture, containing Cu orientation
{112}<111>, S orientation {123}<634>, and brass orientation {011}<112>, forms in three
alloys. Besides, weak cube texture can be observed. In aged alloys, Al–Zn–Mg alloy is
characterized by a strong cube texture, while it is interesting to find that two Sc-enriched
alloys still retain strong rolling texture and the level of the texture density increases as
compared with the cold-rolled alloys. Moreover, �-fiber rolling texture increases with the
increase of Sc additions.
In order to provide more detailed quantitative texture data, the maximum intensities of
orientation distribution function (ODF) f g( ) for a particular angle �1 along the �-fiber
and an angle �2 along the �-fiber are depicted in Fig. 4. It can be seen that there is no
obvious texture in homogenized alloys. The intensity of the rolling texture in two rolled
and aged Sc-enriched alloys is higher than that in the Sc-free alloy. Moreover, the highest
intensity of the �-fiber texture appears at the position of brass orientation, and for the
�-fiber texture, it appears at the position of Cu orientation. With the increase of Sc
additions, the overall �-fiber texture sharpness enhances.
2.3. Microstructure and Microtextures. Figure 5 shows the EBSD microstructures
and the corresponding microtextures of the three aged alloys. The color of each grain is
coded by its crystal orientation based on [001] inverse pole figure as shown in Fig. 5.
As seen from Fig. 5, the microstructure of the aged Al–Zn–Mg alloy is mostly
characterized by coarse recrystallized equiaxed grains with cube texture and weak S
texture, and the average grain size is determined to be about 16.0 m. However, the two
Effects of Sc and Zr on the Texture and Mechanical Anisotropy ...
ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2016, ¹ 1 49
Fig. 2. Mechanical properties of three alloys stretched along different angles from rolling direction:
(a) Al–Zn–Mg; (b) Al–Zn–Mg–0.1Sc–0.1Zr; (c) Al–Zn–Mg–0.25Sc–0.1Zr.
a b
c
50 ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2016, ¹ 1
a b c d e f g h i
Fig. 3. ODFs representative sections of three Al–Zn–Mg alloys under typical thermomechanical
conditions: Al–Zn–Mg [(a) homogenized, (d) cold rolled, (g) aged]; Al–Zn–Mg–0.1Sc–0.1Zr [(b)
homogenized, (e) cold rolled, (h) aged]; Al–Zn–Mg–0.25Sc–0.1Zr [(c) homogenized, (f) cold rolled,
(i) aged].
a b c
d e f
g h i
Fig. 4. Texture evolution of three alloys annealed under typical thermomechanical conditions:
orientation densities f g( )max along �-fiber [(a) homogenized, (b) cold rolled, (c) aged]; orientation
densities f g( )max along �-fiber [(d) homogenized, (e) cold rolled, (f) aged]; exact position of �-fiber
in Euler space [(g) homogenized, (h) cold rolled, (i) aged].
Y. Deng, Z. M. Yin, G. F. Xu, et al.
aged Al–Zn–Mg–Sc–Zr alloys still remain un-recrystallized deformed structure, which
consists of sub-grains with a high fraction of low angle grain boundaries, and have strong
rolling texture. Besides, we can find that the fraction of high angle grain boundaries
decrease with the increase of Sc additions, indicating that Sc additions play an important
role in preventing recrystallization.
Figure 6 shows the TEM microstructures of three aged alloys. Very fine aging phases
in high density were distributed in the interior of grains in three studied alloys. According
to our previous work and reference [9, 10], the ageing precipitates can be identified as
�
phase, which is a metastable hexagonal phase, semi-coherent with the aluminum matrix,
and is the main hardening precipitate in Al–Zn–Mg alloy. Besides, in two Al–Zn–Mg–Sc–Zr
alloys, secondary coherent Al3ScxZr1–x particles in the size of about 20–40 nm, judged by
their Ashby–Brown contrast for bright-field TEM images can be observed. Al3ScxZr1–x
particles can provide effective Zenner pinning force on the migration of grain boundaries
and movement of dislocations. This is the main reason for the reservation of strong rolling
texture in Al–Zn–Mg–Sc–Zr alloys. Moreover, with the increase of Sc additions, the
density for Al3ScxZr1–x particles increases, leading to a lower degree of un-recrystallization.
Besides, except for
� phase, Al3ScxZr1–x particles can further strengthen Al–Zn–Mg–Sc–Zr
alloys, resulting in a higher strength, as shown in Fig. 2.
2.4. Effect of Sc and Zr on Texture during the Preparation of Al–Zn–Mg Alloy
Sheets. For most of liquid metal materials, the final products should be manufactured by
solidification and crystallization processes. During the solidification, the atomic arrangement
of crystallized material changes from a short-range order to a long-range order. The
ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2016, ¹ 1 51
Effects of Sc and Zr on the Texture and Mechanical Anisotropy ...
Fig. 5. EBSD images and the corresponding microtextures of three aged alloys: (a) Al–Zn–Mg;
(b) Al–Zn–Mg–0.1Sc–0.1Zr; (c) Al–Zn–Mg–0.25Sc–0.1Zr.
Fig. 6. TEM microstructures of the three aged alloys: (a) Al–Zn–Mg; (b) Al–Zn–Mg–0.1Sc–0.1Zr;
(c) Al–Zn–Mg–0.25Sc–0.1Zr.
solidification of metals requires two steps: in the first step, ultra-fine crystallites, known as
the nuclei of a solid phase, form from the liquid. In the second step, which can overlap with
the first, the ultrafine solid crystallites begin to grow as atoms from the liquid are attached
to the nuclei until no liquid remains. If the nuclei in the liquid metals are formed
homogeneously, the solidified structure would orientate randomly. This is why there is no
obvious preferred orientation in the homogenized alloys. However, under the industry
casting condition, the grains will range in the direction of heat dissipation, such as the
columnar grains, and thus weak {100} fiber texture is formed, just as shown in Fig. 3. Sc
and Zr additions can’t change the temperature gradient generated during the casting and
solidification. Therefore, they have less effect on the texture of homogenized alloys. During
deformation, the grains rotate as well as elongate, causing certain crystallographic
directions and planes to become aligned with the direction in which stress is applied.
Consequently, after cold rolling, strong rolling textures develop. Besides, in cold rolled
sheet, there is weak cube texture, whose formation can be ascribed to the recovery and
recrystallization process, occurring in hot rolling and annealing before cold rolling. The
recrystallization temperature for Al–Zn–Mg alloy is about 300–400�C. After solution
treatment (470�C/1 h) and aging treatment, full recrystallization occurr in Al–Zn–Mg alloy,
while the two Al–Zn–Mg–Sc–Zr alloys remain fiber deformed grains. Therefore, in aged
alloys, the Al–Zn–Mg alloy is characterized by cube texture, and Al–Zn–Mg–Sc–Zr alloy
mainly consists of rolling texture. The reservation of rolling texture in Al–Zn–Mg– Sc–Zr
alloys is mainly due to the inhibitory effect of Al3ScxZr1–x on recrystallization.
2.5. Effect of Sc and Zr on Mechanical Anisotropy of High Strength Al–Zn–Mg
Alloy Sheets. As seen from Table 1, with the increase of Sc and Zr additions, the
mechanical anisotropy gradually increases. To explain this phenomenon, it should be
related to texture and microstructures.
The deformation resistance of metals is anisotropic. According to Schmid law, the
critical resolved shear stress is given by [11]:
�
�c � cos cos ,� (2)
where � c is critical resolved shear stress, cos cos� � is Schmid factor, � is angle
between the normal to the slip plane and the applied force, � is the angle between the slip
direction and the applied force, and
is yield stress.
For the polycrystal materials, the yield strength can be expressed as
� � �� � � �� � � �gb ss pptM ( ),0 (3)
where ��0 is the critical resolved shear stress (CRSS) of pure Al (about 7 MPa), �
gb ,
�� ss , and �� ppt are the strengthening contribution from subgrain boundaries, solid
solution, and precipitation, respectively, and M is Taylor factor, depending on textures and
orientation of tensile axis. As seen from Eq. (2), to calculate the yield stress under different
tensile direction, it should determine M values. Several models have been proposed to
calculate the M factor of a material at a giving orientation, such as the Sachs model [12],
the Hutchinson model [13], and the Taylor model [14]. However, in our case, the aged
sheet, especially Al–Zn–Mg–Sc–Zr alloys, contains several grain orientations, and based on
authors’ knowledge, no model is available to determine which slip systems will be
activated in each grain for such a case.
In this paper, a new model is proposed with the assumption that all the slip systems
may, with varying probabilities, contribute to plastic deformation, and the slip system with
higher Schmid factor value has a higher chance of being activated. This model can be
expressed as
52 ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2016, ¹ 1
Y. Deng, Z. M. Yin, G. F. Xu, et al.
M f w m f mi j i j random
ji
n
( ) ( ) ,,� ��
��
� ���1
1
12
1
(4)
where M ( )� is the M factor when the angle between the tensile axis and rolling direction
is �, fi is the volume fraction of i texture component, frandom is the fraction of
randomly orientated grains, m is the Schmid factor for random texture (about 0.33). FCC
Al alloys contain four {111} slip planes and three <111> (slip directions) within each
plane, giving 12 slip systems, and mi j, ( )� is the Schmid factor in the order of j when the
angle between the tensile direction and rolling direction is �. The magnitude of mi j, ( )� is
in the order m m m mi i i j i, , , ,( ) ( ) ... ( ) ... ( ),1 2 12� � � �� � � � � where i� 4, j�12. w j is
the weight coefficient for each mi j, ( ),� and satisfies the following condition:
w j
j
�
�
� 1
1
12
, (5)
w
w
m
m
j
j
i j
i j
n
� �
�
�
�
�
�
�
�
�
�
1 1
,
,
, (6)
where n a positive integer, n� 4. During the calculation, we assume that all slip system
participate in slipping, and the higher Schmid factor, the more opportunity to participate in
slipping.
The standard Hall–Petch equation was employed to relate the yield strength of the
material (
) to the average grain size (d),
H P kd�
�� �0
1 2/ . (7)
In this equation,
0 is the intrinsic resistance of the lattice to dislocation motion and k is
a parameter that describes the relative strengthening contribution of grain boundaries. A k
value of 0.04 MPa m� 1 2/ for aluminum was used to estimate the strengthening due to grain
boundaries.
By substituting of k value and grain sizes in three studied alloys obtained from
EBSD, �
gb , the increase in the YS due to the grain boundary strengthening, were 14, 34,
and 42 MPa in Al–Zn–Mg, Al–Zn–Mg–0.1Sc–0.1Zr, and Al–Zn–Mg–0.25Sc–0.1Zr,
respectively.
For peak aged alloys,
� is the aging strengthening phase for Al–Zn–Mg alloy, and in
Al–Zn–Mg–Sc–Zr alloys, there exist two precipitates:
� and Al3ScxZr1–x particles. Value
of � ppt can be calculated as
�
�
�ppt
Gb
r
f
�
2 3
2
, (8)
where � is constant, about 0.36, r is the radius of precipitate (in this study, according to
the TEM images, the sizes of
� and Al3ScxZr1–x were determined to be 12 and 20 nm,
respectively), and f is the volume fraction of precipitates. As there is some difference in
the weight fractions of Zn and Mg among the three alloys, the volume fractions of aging
precipitate are calculated to be 4.19, 3.84, and 4.22% in Al–Zn–Mg, Al–Zn–Mg–0.1Sc–
0.1Zr, and Al–Zn–Mg–0.25Sc–0.1Zr alloys by using JMatPro 5.1 thermodynamic software,
ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2016, ¹ 1 53
Effects of Sc and Zr on the Texture and Mechanical Anisotropy ...
respectively. Moreover, the volume fractions for Al3ScxZr1–x particles are 0.35 and 0.71%
in Al–Zn–Mg–0.1Sc–0.1Zr and Al–Zn–Mg–0.25Sc–0.1Zr alloys, respectively. Therefore,
� �� �ppt ppt� ��MgZn2
135 MPa (Al–Zn–Mg alloy),
� � �� � �ppt ppt ppt� � � � �� �MgZn Al (Sc, Zr)2 3
129 23 152 MPa (Al–Zn–Mg–0.1Sc–0.1Zr
alloy),
� � �� � �ppt ppt ppt� � � � �� �MgZn Al (Sc, Zr)2 3
135 33 168 MPa (Al–Zn–Mg–0.25Sc–0.1Zr
alloy).
Value of �� ss can be calculated as
�� ss KC� 2 3/ , (9)
where K is a constant and C is the average concentration of solute atoms. Combined with
the JMatPro calculation results (the concentrations for solute atoms are about 7.2 wt.% in
solution state and 0.6 wt.% in aged state), �� ss are determined to be 10, 9, and 8 MPa in
Al–Zn–Mg, Al–Zn–Mg–0.1Sc–0.1Zr, and Al–Zn–Mg–0.25Sc–0.1Zr alloys, respectively.
In conclusion, the yield strength for three aged alloys can be calculated by the
following equations:
Al–Zn–Mg:
� �14 152M , (10)
Al–Zn–Mg–0.1Sc–0.1Zr:
� �34 168M , (11)
Al–Zn–Mg–0.25Sc–0.1Zr:
� �42 183M. (12)
Table 2 shows the volume fractions of different texture components in three aged
alloys. It can be found that with the increase of the content of Sc additions the volume
fractions of rolling textures, including S, brass, and Cu orientations, increase, while the
cube and random textures weaken. For the Al–Zn–Mg–0.25Sc–0.1Zr aged sheet, it is
mainly composed of rolling texture components. Table 3 shows the calculated Taylor
factors under different tensile directions.
By substituting the above data into Eqs. (10)–(12), the calculated yield strength under
different angles between tensile direction and rolling direction are shown in Fig. 7. As seen
from Fig. 7, it can be found that the established model can well reflect the internal law
between the yield stress, tensile orientations and texture. Besides, the calculated data are
closer to the experimental data, when n is 4–5 in Al–Zn–Mg alloy, n is 5–6 in
Al–Zn–Mg–0.1Sc–0.1Zr alloy, and n is 6–� in Al–Zn–Mg–0.25Sc–0.1Zr alloy, respectively;
n increases with the increase of Sc and Zr contents. This can be inferred that with the
increase of Sc and Zr additions, only the slipping systems with the higher Schimd factors
have the opportunity to overcome the Zenner pinning of Al3ScxZr1–x particles to participate
in plastic deformation.
54 ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2016, ¹ 1
T a b l e 2
Volume Fractions of Different Texture Components
(Combined with the Results from XRD and EBSD)
Alloy Cu S Brass Cube Random
Al–Zn–Mg 0.018 0.224 0.011 0.275 0.472
Al–Zn–Mg–0.1Sc–0.1Zr 0.175 0.349 0.385 0.022 0.069
Al–Zn–Mg–0.25Sc–0.1Zr 0.200 0.380 0.400 0.000 0.020
Y. Deng, Z. M. Yin, G. F. Xu, et al.
ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2016, ¹ 1 55
T a b l e 3
Values of M under Different Tensile Directions
Alloy 0 30� 45� 60� 90�
n � 4
Al–Zn–Mg 2.803 2.762 2.742 2.767 2.747
Al–Zn–Mg–0.1Sc–0.1Zr 2.879 2.851 2.577 2.885 2.910
Al–Zn–Mg–0.25Sc–0.1Zr 2.891 2.850 2.557 2.890 2.898
n � 5
Al–Zn–Mg 2.781 2.710 2.716 2.716 2.724
Al–Zn–Mg–0.1Sc–0.1Zr 2.810 2.779 2.469 2.812 2.871
Al–Zn–Mg–0.25Sc–0.1Zr 2.817 2.774 2.440 2.815 2.856
n � 6
Al–Zn–Mg 2.764 2.681 2.703 2.687 2.709
Al–Zn–Mg–0.1Sc–0.1Zr 2.759 2.730 2.424 2.764 2.844
Al–Zn–Mg–0.25Sc–0.1Zr 2.762 2.724 2.392 2.764 2.827
n ���
Al–Zn–Mg 2.700 2.600 2.500 2.677 2.656
Al–Zn–Mg–0.1Sc–0.1Zr 2.608 2.554 2.298 2.604 2.755
Al–Zn–Mg–0.25Sc–0.1Zr 2.601 2.538 2.272 2.588 2.732
a b
c
Fig. 7. The caluculated yield stress values and experimental data under different tensile directions:
(a) Al–Zn–Mg; (b) Al–Zn–Mg–0.1Sc–0.1Zr; (c) Al–Zn–Mg–0.25Sc–0.1Zr.
Effects of Sc and Zr on the Texture and Mechanical Anisotropy ...
The Schmid factors of different slipping systems are determined by the textures. The
Al–Zn–Mg–Sc–Zr alloy consists of strong rolling texture components, whose M values are
smaller in case of a 45� angle between rolling direction and tensile direction, and thus the
yield strength value is the lowest under this tensile condition. Moreover, with the increase
of Sc and Zr additions, the volume fractions of S, brass, and Cu orientations increase, while
random texture decreases correspondingly, and thus the mechanical anisotropy enhances.
Conclusions. Texture, mechanical property and microstructure of high strength
Al–Zn–Mg, Al–Zn–Mg–0.1Sc–0.1Zr, and Al–Zn–Mg–0.25Sc–0.1Zr alloys were investigated
by XRD diffraction measurement, tensile tests, transmission electron microscopy and
electron back scattered diffraction methods. The following conclusions can be drawn from
this study.
1. The three homogenized alloys mainly consist of random texture. In cold rolled
alloys, cube orientation and rolling texture are dominant. After solution-aging treatment,
full recrystallization occurs in Al–Zn–Mg alloy and the texture transfers into cube texture.
However, un-recrystallized deformed structures remain in two Al–Zn–Mg–Sc–Zr alloys,
and the alloys have strong �-fiber rolling texture.
2. For aged alloys, the ultimate tensile strength and yield strength increase with
increasing the Sc and Zr additions, meantime, the mechanical anisotropy enhances.
3. To explain the yield strength anisotropy, a new model is established, which can well
reflect the internal law between the yield stress, tensile orientations and texture. It can be
inferred that the preferred orientation is the main factor to mechanical anisotropy. The
higher mechanical anisotropy can be ascribed to the strong �-fiber rolling texture, caused
by the inhibitory effect of nano-scaled Al3ScxZr1–x particles on recrystallization during the
preparation of aged sheets.
Acknowledgments. The authors gratefully acknowledge the financial support from the
National General Pre-research Project of China (51312010402) and the China Postdoctoral
Science Foundation (2014M552149).
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56 ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2016, ¹ 1
Y. Deng, Z. M. Yin, G. F. Xu, et al.
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Received 03.08. 2015
Effects of Sc and Zr on the Texture and Mechanical Anisotropy ...
ISSN 0556-171X. Ïðîáëåìû ïðî÷íîñòè, 2016, ¹ 1 57
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/ENU (Use these settings to create Adobe PDF documents best suited for high-quality prepress printing. Created PDF documents can be opened with Acrobat and Adobe Reader 5.0 and later.)
>>
/Namespace [
(Adobe)
(Common)
(1.0)
]
/OtherNamespaces [
<<
/AsReaderSpreads false
/CropImagesToFrames true
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(InDesign)
(4.0)
]
/OmitPlacedBitmaps false
/OmitPlacedEPS false
/OmitPlacedPDF false
/SimulateOverprint /Legacy
>>
<<
/AddBleedMarks false
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/ConvertColors /ConvertToCMYK
/DestinationProfileName ()
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/Downsample16BitImages true
/FlattenerPreset <<
/PresetSelector /MediumResolution
>>
/FormElements false
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/MultimediaHandling /UseObjectSettings
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/PDFXOutputIntentProfileSelector /DocumentCMYK
/PreserveEditing true
/UntaggedCMYKHandling /LeaveUntagged
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/UseDocumentBleed false
>>
]
>> setdistillerparams
<<
/HWResolution [2400 2400]
/PageSize [612.000 792.000]
>> setpagedevice
|