ISSN: 2641-6921
Furong Cao1*, Guoqiang Xue2 and Bijin Zhou3
Received: October 23, 2021; Published: November 2, 2021
*Corresponding author: Furong Cao, School of Materials Science and Engineering, Northeastern University, Shenyang 110819, PR China
DOI: 10.32474/MAMS.2021.04.000198
Friction stir processing is one of the severe plastic deformation methods. Static grain growth study during friction stir processing does not receive enough attention compared to dynamic recrystallization study. Thus, in this report on static grain growth kinetics of Mg-Li alloy, an ultralight Mg-8.41Li-1.80Al-1.77Zn alloy has been fabricated by rolling, friction stir processing, and annealing. Microstructural examination of the nugget zone in the annealed state revealed that the grain growth rates at 523 and 573 K are much lower than the growth rate at 623 K. In the meantime, grain growth prior to 30 min is not obvious, but grains grow obviously with the increase in time after 30 min. The nugget zone grain growth kinetics equation abided by parabolic relation based on the linear fitting of the experimental grain sizes. The grain growth activation energy was 176.191 kJ/mol, higher than the lattice diffusion activation energy of magnesium, 135 kJ/mol. Probable cause is that the second phase particles increase the difficulty of thermal activation and raise the activation energy. The calculation error between theoretical grain growth model and experimental grain growth model is two orders of magnitude because of the use of an effective diffusivity. Hence, accurate theoretical model for static grain growth remains to be established in the future. This indirectly demonstrates the scientific meaning and value of established experimental parabolic growth model.
Keywords: Magnesium-lithium alloy; Friction stir processing; Annealing; Static grain growth; Microstructure
Mg-Li alloy is the lightest nontoxic metallic alloy. Due to extremely low density, excellent specific stiffness, good specific strength, good damping property, and electromagnetic shielding performance, Mg-Li alloy has the potential for applications in aerospace, military weapons, 3C products, and automobile manufacturing fields. Thus, study on Mg-Li alloy has drawn much attention from extensive researchers [1-7]. Not only room temperature mechanical properties, corrosion performance, and microstructures [1,4,5,6] but also high temperature behavior and microstructure [2,3,7] were investigated. Because of good comprehensive mechanical properties of two-phase Mg-Li alloys, we designed an Mg-8Li-2Al-2Zn (designated as LAZ822) alloy. The purpose of 8 wt. %Li addition is to obtain a two-phase alloy. The purpose of 2 wt.% Al addition is to achieve solid solution strengthening and second phase strengthening. The purpose of 2 wt.% Zn addition is to achieve solid solution strengthening. Friction stir processing (FSP) is further development of friction stir welding and one of the severe plastic deformations (SPD) approaches. According to literature survey, FSP of Mg-Li alloys has been reported in several alloys [8-10]. The research aspect includes ambient mechanical properties, corrosion behavior, and microstructures [8] and high temperature mechanical properties and microstructures [9-10] during FSP. Thermal stability issue is often accompanied by SPD process. When the ultrafine-grained and fine-grained alloys are exposed to high temperature, grain coarsening often occurs. Some grain growth reports and review containing modelling and experimental microstructures were documented [11-14]. To the best of our knowledge, no information has been known about the study on the static grain growth behavior in Mg-Li alloy. Thus, it is necessary to work out this report on static grain growth in Mg-Li alloy. In this work. our investigated contents include four aspects: (i) to fabricate LAZ822 alloy by casting, rolling, FSP, annealing; (ii) to investigate or characterize its annealing microstructure; (iii) to investigate its grain growth kinetics; (iv) to compare established experimental grain growth equation and theoretical grain growth equation. It is hoped that this first report about static grain growth in Mg-Li alloy processed by FSP stimulates the interests of extensive Mg-Li researchers.
The present LAZ822 alloy ingot was obtained by melting and casting process similar to the process of Mg-9.3Li-1.79Al-1.61Zn alloy ingot, as shown elsewhere in detail [15]. The analyzed chemical composition of this alloy was 8.41 mass % Li, 1.80 mass % Al, 1.77 mass % Zn and balanced Mg. The ingot was homogenized at 473 K for 20 h. After milling of the ingot surfaces, the billet with the dimensions of 24 mm×90 mm×170 mm was held at 573 K for 2 h. Then the billet was hot rolled at 573 K for 12 passes to 6 mm thickness with a percent reduction of 75%. The schematic diagram of FSP principle was shown in [10]. A rotating tool was inserted into the plate to cause intense plastic deformation at elevated temperature and achieve microstructural modification. FSP was conducted on the hot rolled plate. Water spray cooling in the working position of the plate was the cooling mode. The diameter of conical pin was 8 mm. The rotational speed of the stirring head was 800 rpm. The transverse speed of the stirring head was 45 mm/ min. The rolled samples were annealed at 523, 573, and 623 K for 10-200 min. To observe the optical microstructure, the specimens were mechanically ground and polished by abrasive papers from 100# to 3000#. The etched solution was 10% HCl+90% alcohol. After etched, the specimens were rinsed by alcohol and dried by a hair drier. Olympus DSX500 optical microscope was used for the examination. Grain sizes were measured by Image-Pro Plus (IPP) software to characterize the microstructures.
Experimental static grain growth after FSP (Figures 1,2, 3) display the nugget zone microstructures of FSP LAZ822 alloy annealed at temperatures of 523, 573, and 623 K for holding times of 10, 30, and 60 min. The white phase is hexagonal closed-packed (HCP) structured α-Mg solid solution phase while the yellow phase is body-centered cubic (BCC) structured β-Li solid solution phase. Hence, this alloy is a two-phase alloy. It is noted that grain size increases with the rise in temperature. This is because increased temperature accelerates atomic diffusion and boundary migration, and boundary migration results in grain growth. In particular, the grain sizes at 573 and 623 K differ greatly, indicating that the grain size is very sensitive to the temperature. (Figure 4) presents the nugget zone microstructures of FSP LAZ822 alloy annealed at 623 K for different holding times. It is clear that grains grow with the increase in holding time. Table 1 presents the grain sizes after annealing at different temperatures and holding times. According to (Figures 1-4) and Table 1, grain size is very sensitive to annealing temperature and holding time. (Figure 5) presents the variation in grain sizes of LAZ822 alloy with different temperatures and times. It is seen that grain size increases with the temperatures. The growth rates, the slope of the curves, at 523 and 573 K are much lower than the growth rate at 623 K. In the meantime, grain growth prior to 30 min is not obvious, but grains grow obviously with the increase in time after 30 min.
Figure 1: Nugget zone microstructures of FSP LAZ822 alloy annealed at different temperature for holding time of 10 min: (a) 523K; (b) 573K; (c) 623K.
Figure 2: Nugget zone microstructures of FSP LAZ822 alloy annealed at different temperature for holding time of 30 min: (a) 523K; (b) 573K; (c) 623K.
Figure 3: Nugget zone microstructures of FSP LAZ822 alloy annealed at different temperature for holding time of 60 min: (a) 523K; (b) 573K; (c) 623K.
Figure 4: Nugget zone microstructures of FSP LAZ822 alloy annealed at 623 K for different holding times: (a)30 min; (b)60 min; (c)100 min; (d)150 min.
Establishment of Grain Growth Kinetics Models According To Experimental Data
Static grain growth kinetics model is given by the following form:
where D and D0 are the average grain size after holding time, t, and initial grain size before annealing, respectively; k is the grain growth factor, and q is the grain growth exponent, relevant to the mechanism controlling the grain growth. Differentiating Eq. (1) by time, t, one gets
According to Table 1, ln (dD/dt)-ln (D) curves can be plotted, and hence k and q can be obtained. (Figure 6) presents the ln (dD/dt)-ln (D) curves of FSP and annealed LAZ822 alloy. q values at 523, 573, and 623 K are equal to 2. Thus, the grain growth abides by parabolic curve. Generally, q values are 2,3,4,5, and 6 for conventional alloys. Large q values mean lower growth rate. In the present alloy, q =2 means pronounced grain growth.
Thus, the static grain growth models were established as follows:
where k values are 0.075, 0.299, and 3.69 μm2/min at 523, 573,
and 623 K, respectively.
k value is given by
where k0 is a constant, R is the universal gas constant, 8.314 J/
mol•K, and T is the absolute temperature in Kelvin.
(Figure 7) presents the ln k -1000/T curve of FSP and annealed
LAZ822 alloy. The slope of fitted curve is 21.192. Thus, the grain
growth activation energy, Qg, is calculated as the following:
Qg=21.192×8.314×1000=176.191 kJ/mol. This experimental grain
growth activation energy of 176.191 kJ/mol is higher than the
lattice diffusion activation energy of magnesium, 135 kJ/mol [16].
Probable cause is that the second phase particles obstruct the
movement of grains and increase the difficulty of softening such
as annealing after FSP. In other words, the second phase particles
increase the difficulty of thermal activation and raise the activation
energy.
Analysis and Comparison Of Theoretical And Experimental Static Grain Growth Equations
Theoretical static grain growth model for parabolic growth curve is given by [17]
where d is the grain size after holding time of t; d0 is the initial
grain size for t=0 s; γ is the grain boundary surface tension; Ω is the
atomic volume; W is the grain boundary width, W=2b, here, b is the
magnitude of Burgers vector; Dgb is the grain boundary diffusivity;
kB is Boltzmann’s constant; k is the growth factor.
An estimation is made for 573 K × 60 min situation. T=573
K, t=3600 s, d=3.45 μm, d0=1.52 μm, γ=1 J m-2 [18], b=3.21×10-
10 m [19] ,Ω=0.7b3=2.315×10-29 m3, Dgb=6.34×10-11 m2 s-1 [20], kB
=1.38×10-23 J K -1. The theoretical k value is 1.16×10-9 m2 s-1 while
the experimental k value is 2.66×10-15 m2 s-1. This indicate a big
diffrerence. This is because the diffusion process is not a grain
boundary diffusion process but a lattice diffusion dominated
process. Further estimation is made using an effective diffusivity
in [21]. Deff=DL+(W/d)Dgb, where Deff is the effective diffusivity and
DL is the lattice diffusivity. DL=4.27×10-15 m2 s-1 according to our
previous model [20]. The theoretical k value is 2.93×10-13 m2 s-1
while the experimental k value is 2.66×10-15 m2 s-1. The calculation
error between theortical model and experimental model becomes a
little bit closer and is two orders of magnitude because of the use of
an effective diffusivity. Hence, accurate theoretical model for static
grain growth remains to be established in the future. As Atkinson
[22] and Baldan [23] pointed out in their articls published in
1988 and 2002, respectively, that an unified accurate grain growth
model still was not avaliable although much effort has been made
across the world. Our calculated results confirm what they said.
This indirectly demonstrates the scientific meaning and value of
established experimental parabolic growth model.
a. An ultralight Mg-8.41Li-1.80Al-1.77Zn alloy has been
fabricated by rolling, friction stir processing, and annealing.
Microstructural examination of the nugget zone in the annealed
state revealed that the grain growth rates at 523 and 573 K are
much lower than the growth rate at 623 K. In the meantime, grain
growth prior to 30 min is not obvious, but grains grow obviously
with the increase in time after 30 min.
b. The nugget zone grain growth kinetics equation abided by
parabolic relation based on the linear fitting of the experimental
grain sizes. The grain growth activation energy was 176.191 kJ/mol,
higher than the lattice diffusion activation energy of magnesium,
135 kJ/mol. Probable cause is that the second phase particles
increase the difficulty of thermal activation and raise the activation
energy.
c. The calculation error between theortical grain growth
model and experimental grain growth model is two orders of
magnitude because of the use of an effective diffusivity. Thus,
accurate theoretical model for static grain growth remains to be
established in the future. This indirectly demonstrates the scientific
meaning and value of established experimental parabolic growth
model.
National Natural Science Foundation of China (No.51334006).
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