# Effect of Compressive Strain Rate on Microstructure and Mechanical Properties of 7050 Aluminium Alloy

Authors: Qiang Shen; Luochuang Huang; Yan Li; Kang Yu; Dezheng Liu
Journal: Advances in Materials Science and Engineering
 (2021)

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## Abstract

7050 aluminium alloy is a superior material used in the areas of aerospace and automobile manufacturing. In this work, homogeneous cast cylinder samples of 7050 aluminium alloy with size of Φ80 mm × 100 mm were compressed isothermally at 350°C with compressive strain rate of 0.1 s−1,1 s−1, and 10 s−1, respectively. The samples were then processed into standard tensile specimens, and then tensile testing was done by using the GL8305 universal testing machine. The grain sizes and fracture morphology were analyzed by the SEM observation and cellular automaton (CA) method. The effect of compressive strain rate on microstructure and mechanical properties of 7050 aluminium alloy was investigated. The results show the following. (1) Grain refinement occurred after compression. The grain sizes of the samples decrease with the decrease of compressive strain rate. The grain sizes in the radial edge and the axial center of the cylinder samples are the smallest. (2) The tensile strength and breaking elongation rate were improved when compared to the original alloy. The mechanical properties of samples compressed with compressive strain rate of 0.1 s−1 are the best. (3) The fracture morphology of the samples shows that the fracture of the samples is ductile fracture. The sizes and depths of dimples increased with the decrease of grain sizes.


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## Body

## 1. Introduction

7050 aluminium alloy is widely used in the fields of aerospace, automobile manufacturing, high-speed rail manufacturing, and shipping industry due to its high strength, good toughness, excellent corrosion resistance, and lightweight [1–4]. Hot extrusion is one of the main plastic forming process methods for manufacturing 7XXX series aluminium alloy with high performance [5–7]. The parameters of hot extrusion, such as extrusion speed, processing temperature, extrusion pressure, and so on, largely affect the properties of aluminium alloy.In the past decades, research studies have been done to investigate microstructure evolution and mechanical properties of aluminium alloy processed by the hot compression process. The microstructure of aluminium alloys usually experiences dynamic recrystallization (DRX) during the hot extrusion process. Chen et al. [8] investigated the microstructural evolution under compression tests over a wide range of strain rates. Work hardening deceases with the increase of strain rate. Dynamic recrystallization with grain refinement and phase transition occurred during compression. Li et al. [9] found that the fraction of DRX increased with decrease of strain rate, and Huang et al. [10] found that the percentage of DRX increased with the rise of temperature. Zhao et al. [7] found that the recrystallization mechanism during isothermal compression changed from continuous dynamic recrystallization to discontinuous dynamic recrystallization mechanism as the strain rate decreased from 10−3 s−1 to 5 × 10−6 s−1. Cardoso et al. [11] compared the grain sizes and hardness of 7050 aluminium alloy process with equal channel angular pressing (ECAP) at room temperature and 150°C. The sample pressed at 150°C has more refined grains and larger hardness. Yunzhong et al. [12] investigated the grain evolution at different parts of the 7050 aluminium alloy cylinder sample and the result shows the deformation of grain at the central part get larger when the strain increased while the grains becomes smaller and more homogeneous. However, the evolution of grains associated with strain distribution at different parts of cylinder samples during hot compression is much more complicated. Thus, the evolution of grains of cylinder aluminium alloys needs to be researched in greater detail. The mechanical properties of alloy are largely related to the microstructure, such as the grain shape, and the type and orientation of texture. Branco et al. [13] researched the effect of strain ratio on cyclic deformation behaviour of 7050 aluminium alloy. The material exhibited a cyclic strain softening behaviour, and the microstructure shows mainly elongated grains aligned with the rolling direction with a certain degree of recrystallization. Wei et al. [14] found that the yield strength in the center of the cylinder sample with a large grain size is higher than that at the edge with the smaller grain size in the thickest section of the cylinder. This is because the effect of texture on the yield strength overweighed the refinement strengthening, where copper-orientated ({112} < 111>) deformation texture with better yield strength dominated the center area and cube-orientated ({112} < 111>) recrystallized texture dominated at the edge. Few investigations have studied the tensile strength and tensile fracture combined with evolution of microstructure of compressed 7050 aluminium alloy. Additional research studies are important to explore the relationship between mechanical behaviours and microstructure of 7050 aluminium alloy resulted from hot compression during the tensile experiment.In our work, 7050 aluminium alloy cylinder samples with size ofφ80 mm × 100 mm were isothermally compressed with three strain rates (0.01 s−1, 0.1 s−1, and 1 s−1) at 350°C. The total strain value of the compression is 0.6. The cylinder samples are then processed to standard tensile specimens at room temperature. Tensile testing was done by using the GL8305 universal testing machine. The microstructure and the grain evolution were observed via EBSD and simulated with the CA method. The effect of strain rate on alloy microstructure and mechanical properties was investigated. The fracture was characterized and analyzed.


## 2. Mathematical Modelling

### 2.1. Constitutive Model and Dynamic Recrystallization Model

The high-temperature rheological behaviour of 7050 aluminium alloy is not only related to the composition of chemical elements but also affected by the deformation temperature and strain rate. The Arrhenius model [15] is used to describe the high-temperature rheological behaviour of aluminium alloy in this work. It is mathematically expressed as follows:(1)ε˙=Asinhασnexp−QRT,where A, b, and n are material constants, which can be calculated via isothermal uniaxial tensile test, ε˙ and σ are the strain rate and the stress, Q is the activation energy of deformation (kJ/mol), T is the temperature (K), and R is the gas constant, which is 8.314 J/(mol·K).Nucleation of dynamic recrystallization is a complicated process which usually occurs locally in the deformed matrix. The decrease of dislocation density causes the decrease of free energy of the sample while formation of new intersurface between new crystal nuclei and the matrix leads to the increase of free energy [16].The model of dynamic recrystallization can be expressed as follows:(2)drex=x1d0b1εn1ε˙m1expQ1RT,(3)Xdrx=1−exp−βdε−x2εpε0.5kd,(4)ε0.5=x3d0b2εn2ε˙m2expQ2RT,where x1, x2, x3, b1, b2, n1, n2, m1, m2, βd, and kd are material constants in the recrystallization model, which can be obtained from isothermal uniaxial tensile test, d0 is the original grain size of 7050 aluminium alloy (its value is ∼70 μm), Q1 and Q2 represent the activation energy of grain growth and the activation energy of recrystallization (kJ/mol), ε0.5 is the strain when volume fraction of dynamic recrystallization reaches 50%, and εp is peak strain of dynamic recrystallization which can be calculated by the following formula:(5)εp=x4d0b3ε˙m3expQ3RT,where x4, b3, and m3 are material parameters, which can be calculated by second derivative of the function between strain hardening rate and stress. For more details on the aforementioned parameters of 7050 aluminium alloy, the readers are referred to reference [17], and the values are shown in Table 1.Table 1
The value of parameters of the dynamic recrystallization model.
x1x2x3x4b1b2b3n1n2m1m2m3βdkdQ1 (kJ/mol)Q2 (kJ/mol)Q3 (kJ/mol)125.80.4910.001360.0255−0.00495−0.3640.12300−0.01030.1920.06710.6932.112311.013380.816844.7


### 2.2. Cellular Automaton (CA) Method

Cellular automaton method is a mathematical model of dynamic system which is discrete in time and space. It consists of five fundamental concepts: cellular unit, cellular state, cellular neighbour type, cellular space, and cellular transition rules. The cellular unit is defined as 2.5μm × 2.5 μm square.The cellular state contains the state variablei and the direction variable j. The cellular unit is solid state if the variable i = 1 and the cellular unit is liquid if i = 0. The value of j is any integer between 0–180, and each integer represents a specific orientation. The cellular space is defined as a square cellular grid with cellular unit number of 400 × 400. Thus, the space size of cellular space is 1 mm × 1 mm according to the cellular unit size of 2.5 μm. The state of the neighbouring cellular units at specific moment t can be expressed as follows:(6)γCit=fγC1t−Δt,γC2t−Δt,γC3t−Δt,…,γCkt−Δt,γCit−Δt,where γCit−Δt represents the state of the cellular unit at specific moment t, Ck is the Kth neighbour of the cellular unit, f is the functional relationship, and Δt is the variation of time.


## 2.1. Constitutive Model and Dynamic Recrystallization Model

The high-temperature rheological behaviour of 7050 aluminium alloy is not only related to the composition of chemical elements but also affected by the deformation temperature and strain rate. The Arrhenius model [15] is used to describe the high-temperature rheological behaviour of aluminium alloy in this work. It is mathematically expressed as follows:(1)ε˙=Asinhασnexp−QRT,where A, b, and n are material constants, which can be calculated via isothermal uniaxial tensile test, ε˙ and σ are the strain rate and the stress, Q is the activation energy of deformation (kJ/mol), T is the temperature (K), and R is the gas constant, which is 8.314 J/(mol·K).Nucleation of dynamic recrystallization is a complicated process which usually occurs locally in the deformed matrix. The decrease of dislocation density causes the decrease of free energy of the sample while formation of new intersurface between new crystal nuclei and the matrix leads to the increase of free energy [16].The model of dynamic recrystallization can be expressed as follows:(2)drex=x1d0b1εn1ε˙m1expQ1RT,(3)Xdrx=1−exp−βdε−x2εpε0.5kd,(4)ε0.5=x3d0b2εn2ε˙m2expQ2RT,where x1, x2, x3, b1, b2, n1, n2, m1, m2, βd, and kd are material constants in the recrystallization model, which can be obtained from isothermal uniaxial tensile test, d0 is the original grain size of 7050 aluminium alloy (its value is ∼70 μm), Q1 and Q2 represent the activation energy of grain growth and the activation energy of recrystallization (kJ/mol), ε0.5 is the strain when volume fraction of dynamic recrystallization reaches 50%, and εp is peak strain of dynamic recrystallization which can be calculated by the following formula:(5)εp=x4d0b3ε˙m3expQ3RT,where x4, b3, and m3 are material parameters, which can be calculated by second derivative of the function between strain hardening rate and stress. For more details on the aforementioned parameters of 7050 aluminium alloy, the readers are referred to reference [17], and the values are shown in Table 1.Table 1
The value of parameters of the dynamic recrystallization model.
x1x2x3x4b1b2b3n1n2m1m2m3βdkdQ1 (kJ/mol)Q2 (kJ/mol)Q3 (kJ/mol)125.80.4910.001360.0255−0.00495−0.3640.12300−0.01030.1920.06710.6932.112311.013380.816844.7


## 2.2. Cellular Automaton (CA) Method

Cellular automaton method is a mathematical model of dynamic system which is discrete in time and space. It consists of five fundamental concepts: cellular unit, cellular state, cellular neighbour type, cellular space, and cellular transition rules. The cellular unit is defined as 2.5μm × 2.5 μm square.The cellular state contains the state variablei and the direction variable j. The cellular unit is solid state if the variable i = 1 and the cellular unit is liquid if i = 0. The value of j is any integer between 0–180, and each integer represents a specific orientation. The cellular space is defined as a square cellular grid with cellular unit number of 400 × 400. Thus, the space size of cellular space is 1 mm × 1 mm according to the cellular unit size of 2.5 μm. The state of the neighbouring cellular units at specific moment t can be expressed as follows:(6)γCit=fγC1t−Δt,γC2t−Δt,γC3t−Δt,…,γCkt−Δt,γCit−Δt,where γCit−Δt represents the state of the cellular unit at specific moment t, Ck is the Kth neighbour of the cellular unit, f is the functional relationship, and Δt is the variation of time.


## 3. Experiment and Simulation Method

### 3.1. Materials and Experiment Method

The 7050 aluminium alloy was provided by Southwest Aluminium Group Co. Ltd. The alloy ingots were slowly heated to 470°C at the rate of 0.5°C/s and were annealed for 24 h. Then, alloy ingots were then water cooled to room temperature. The heat treatment process helped to preserve the homogenized structure and prevent element segregation near the grain boundary. After homogenization treatment, 7050 aluminium alloy ingots were processed to cylinder samples with size of Φ80 mm × 100 mm. The chemical composition of the alloy was characterized by the PDA-5500S Shimadzu spectrum analyzer.The chemical composition of the sample conforms to 7050 aluminium alloy according to the standard GB/T3190-1996, which is displayed in Table2.Table 2
The chemical composition of 7050 aluminium alloy (wt%).
Chemical elementsZnCuMgZrTiSiFeAlActual values (wt%)6.652.542.540.140.0580.130.15RemainsGB/T3190-19965.7∼6.72.0∼2.61.9∼2.60.08∼0.150.060.120.15RemainsThe single-pass compression test of the cylinder samples was done by using the thermal physics simulator Gleeble 1500. Thermocouples were welded on the side of the samples to monitor and collect test temperatures. The compression tests were done by using the thermal physics simulator Gleeble 1500. The samples were heated to 350°C at a rate of 10°C/s and annealed for 60 s to reduce anisotropy before compression. The cylinder samples were compressed at different rates (0.1 s−1, 1.0 s−1, and 10.0 s−1) until the total tensile strain reached 0.6. The grains in the different parts of the cylinder samples were observed and compared with electron backscattering diffraction (EBSD). Standard tensile specimens were prepared from the cylinder samples according to standard of DB52/T 926-2014. These tensile specimens were taken from the central axis of the cylinder, and the sampling location is shown in Figure 1(a). The detailed size parameters of the standard tensile specimen are shown in Figure 1(b). Tensile testing was performed to examine the mechanical properties of these compressed samples.Figure 1
The sampling position (a) and the size diagram (b) of standard tensile specimen (mm).The quasistatic tensile test of specimens was carried out on the GL8305 universal testing machine. The mechanical parameters: tensile strength and fracture derivation rate, were measured according to GB/T228.1-2010 [18]. The fracture was electrochemically polished with an electrolyte solution mixed with 10% perchlorate and 90% ethanol. The voltage, the current, and the time of electrolytic polishing are 26 V, 1.2 A, and 4 s, respectively. Then, the specimen was anodically coated with a solution which consists of 5 mL fluoroborate and 200 mL deionized water. The voltage, the current, and the time of coating are 25 V, 1.5 A, and 50 s. Then, the fracture was ultrasonically cleaned after electrochemical polishing and anodical coating. The fracture was observed by using the JSM-6510 scanning electron microscope (SEM).


### 3.2. Finite Element Model

The thermal compression process and grain evolution of 7050 aluminium alloy cylinder were simulated in the software DEFORM 3D V6. The high-temperature rheological model of the material was assigned according to formula (1), and the dynamic recrystallization model was assigned according to formulas (2)∼(5). The cylinder rod was premeshed in the software Hypermesh14.0. The mesh elements were mainly in a hexahedral shape, and the grids at the notch were locally densified. The total number of the grids was 36278. The punch and the die were set as rigid bodies. The temperature was set at 350°C. The die was fixed, and the punch moved at speeds of 1 mm/s, 10 mm/s, and 100 mm/s, respectively. The punch stopped moving until the nominal strain reached 0.6. The results of the previous step were imported into the postprocessing microstructure simulation module. The evolution of alloy grains during the tensile test was simulated via the cellular automaton (CA) method. The plastic damage and mechanism of grain evolution were investigated.


## 3.1. Materials and Experiment Method

The 7050 aluminium alloy was provided by Southwest Aluminium Group Co. Ltd. The alloy ingots were slowly heated to 470°C at the rate of 0.5°C/s and were annealed for 24 h. Then, alloy ingots were then water cooled to room temperature. The heat treatment process helped to preserve the homogenized structure and prevent element segregation near the grain boundary. After homogenization treatment, 7050 aluminium alloy ingots were processed to cylinder samples with size of Φ80 mm × 100 mm. The chemical composition of the alloy was characterized by the PDA-5500S Shimadzu spectrum analyzer.The chemical composition of the sample conforms to 7050 aluminium alloy according to the standard GB/T3190-1996, which is displayed in Table2.Table 2
The chemical composition of 7050 aluminium alloy (wt%).
Chemical elementsZnCuMgZrTiSiFeAlActual values (wt%)6.652.542.540.140.0580.130.15RemainsGB/T3190-19965.7∼6.72.0∼2.61.9∼2.60.08∼0.150.060.120.15RemainsThe single-pass compression test of the cylinder samples was done by using the thermal physics simulator Gleeble 1500. Thermocouples were welded on the side of the samples to monitor and collect test temperatures. The compression tests were done by using the thermal physics simulator Gleeble 1500. The samples were heated to 350°C at a rate of 10°C/s and annealed for 60 s to reduce anisotropy before compression. The cylinder samples were compressed at different rates (0.1 s−1, 1.0 s−1, and 10.0 s−1) until the total tensile strain reached 0.6. The grains in the different parts of the cylinder samples were observed and compared with electron backscattering diffraction (EBSD). Standard tensile specimens were prepared from the cylinder samples according to standard of DB52/T 926-2014. These tensile specimens were taken from the central axis of the cylinder, and the sampling location is shown in Figure 1(a). The detailed size parameters of the standard tensile specimen are shown in Figure 1(b). Tensile testing was performed to examine the mechanical properties of these compressed samples.Figure 1
The sampling position (a) and the size diagram (b) of standard tensile specimen (mm).The quasistatic tensile test of specimens was carried out on the GL8305 universal testing machine. The mechanical parameters: tensile strength and fracture derivation rate, were measured according to GB/T228.1-2010 [18]. The fracture was electrochemically polished with an electrolyte solution mixed with 10% perchlorate and 90% ethanol. The voltage, the current, and the time of electrolytic polishing are 26 V, 1.2 A, and 4 s, respectively. Then, the specimen was anodically coated with a solution which consists of 5 mL fluoroborate and 200 mL deionized water. The voltage, the current, and the time of coating are 25 V, 1.5 A, and 50 s. Then, the fracture was ultrasonically cleaned after electrochemical polishing and anodical coating. The fracture was observed by using the JSM-6510 scanning electron microscope (SEM).


## 3.2. Finite Element Model

The thermal compression process and grain evolution of 7050 aluminium alloy cylinder were simulated in the software DEFORM 3D V6. The high-temperature rheological model of the material was assigned according to formula (1), and the dynamic recrystallization model was assigned according to formulas (2)∼(5). The cylinder rod was premeshed in the software Hypermesh14.0. The mesh elements were mainly in a hexahedral shape, and the grids at the notch were locally densified. The total number of the grids was 36278. The punch and the die were set as rigid bodies. The temperature was set at 350°C. The die was fixed, and the punch moved at speeds of 1 mm/s, 10 mm/s, and 100 mm/s, respectively. The punch stopped moving until the nominal strain reached 0.6. The results of the previous step were imported into the postprocessing microstructure simulation module. The evolution of alloy grains during the tensile test was simulated via the cellular automaton (CA) method. The plastic damage and mechanism of grain evolution were investigated.


## 4. Results and Discussion

### 4.1. The Evolution of Microstructure

Figure2 shows the grain images oriented at the axial center of the cylindrical sample. Figures 2(a)–2(d) show the grain structure photographed by EBSD technique, and Figures 2(e)–2(h) show the simulated grain structure derived from the CA simulation technique. Figure 2(e) shows undeformed grains of raw aluminium alloy with mean sizes of ∼70 μm. The structures in Figures 2(b), (c) and (d) indicate that the grains of the compressed samples were refined after plastic deformation. As shown in Figure 2(b), coarse grains of samples loaded with a strain rate of 0.01 s−1 were crushed. A large number of fine grains appeared both inside the grains and near the grain boundary, which showed equiaxed shape. It reflects that dynamic recrystallization was fully finished in this sample. The microstructure of samples processed with strain rate of 0.1 s−1 at 350°C (Figure 2(c)) reveals that a lot of coarse grains were squeezed. A small number of fine grains appeared near the boundary of coarse grains, suggesting that dynamic recrystallization partially happened. In Figure 2(d), fine grains nucleated near the grain boundaries of most of the grains. It indicates that the dynamic recrystallization was about to happen. Table 3 shows the statistic of mean grain size derived from the EBSD and CA simulation method. The data of Table 3 and the insets in Figure 2 indicate that the mean grain sizes simulated by CA are consistent with the results of the images taken by EBSD. The deviation of mean grain sizes between two ways is smaller than 5%.Figure 2
The grain images in the axial center of the cylindrical samples compressed at 350°C with (a) no strain rate (raw structure); (b) compressive strain rate of 0.01 s−1; (c) compressive strain rate of 0.1 s−1; (d) compressive strain rate of 1.0 s−1. The CA simulated microstructure of samples compressed at 350°C with (e) no strain rate; (f) compressive strain rate of 0.01 s−1; (g) compressive strain rate of 0.1 s−1; (h) compressive strain rate of 1.0 s−1.Table 3
The mean grain size from EBSD and CA simulation.
Strain rate (mm/mm)Mean grain size (EBSD,μm)Mean grain size (CA,μm)Deviation (%)07070—0.0125.624.54.30.132.631.53.4144.842.64.9When the compressive rate is small, grain refinement in the alloy driven by the dynamic recrystallization mechanism can fully take place. The recrystallization process is attributed to sufficient degree of freedom for rotation and rearrangement of grain nuclei and subgrains [19]. When the compressive rate increases, there is low degree of freedom for rotation and rearrangement of grain nuclei and subgrains. High dislocation density-induced work hardening mechanism dominates the evolution of inner structure while there is not enough time to trigger the dynamic recrystallization of grains. In consequence, grains with small sizes are only formed around the grain boundaries in the samples compressed with high rate, as shown in Figure 2(d). The refinement of alloy grains can be realized by decreasing the compressive rate to improve dynamic recrystallization effect.Figure3 shows the grain size distribution along the axial and the radial directions of the sample loaded with compressive strain rate of 0.01 s−1 at 350°C. The strains and grain sizes of spots P1∼P7 are analyzed. The image of upper surface shows that the grains at the edge of the surface are the finest. The grain size increased from the edge to the center along the radial direction. The value increases from 2.38 μm to 50.3 μm. The axial change of grains indicates that the grain size increases from the cylinder center to both sides of the cylinder axially. This is because both sides of the sample were in contact with the punch and the die, respectively. The friction between the contact surfaces during plastic deformation obstructs the radial migration of atoms, which leads to the axial reduction of strain. The end face of the cylinder sample is a freely deformed surface with no obstruction of friction. Therefore, it migrates outside during the deformation. Furthermore, the local strain at the edge of upper and bottom surfaces of the sample also increased because of the “pull effect” from the end face of the cylinder. The strain distribution is shown by the coloured strain pattern of cylinder sample with strain rate of 0.01 s−1 at 350°C as shown in Figure 4. The sample in Figure 4 presents a bulge shape. The strain is the largest at the edge of the upper and bottom surfaces and at the center of the samples. The strain is the smallest at the center of the upper and bottom surfaces. The grain refinement is closely related to the strain distribution. The larger the strain is, the higher the grain refinement is.Figure 3
The grain size distribution of the cylinder sample with strain rate of 0.01 s−1 at 350°C.Figure 4
The coloured strain pattern of the cylinder sample with strain rate of 0.01 s−1 at 350°C.Figure5 shows the curve of strain vs. deformation time of the sample with compressive strain rate of 0.01 s−1 at 350°C. Data of spots P1–P5 marked in Figure 5 were collected. The strain of P1 is 1.78 which is the largest of the alloy after deformation. The largest strain value of P4 after deformation is 1.64. The strains of P2, P3, and P5 show a similar curve as shown in Figure 5. Figure 6 shows the strain distribution along the axial and radial directions. The radial direction takes the center of the circle on the upper surface as the origin point, and the axial direction takes the center of the cylinder as the origin point. The radial curve indicated that the strain of about 80% of spots kept a value of ∼0.5 mm/mm. The strain along the axial direction decreases from the center to both sides evenly.Figure 5
Curve of strain vs. deformation time of spots derived from Figure4 (P1∼P5).Figure 6
Strain deformation along axial and radial directions of the cylinder.Figure7 shows the grain size distribution along axial (Figure 7(a)) and radial (Figure 7(b)) directions with different compressive strain rates. The distribution of grain sizes is in great agreement with distribution of strain. As shown in Figure 7(a), the grain sizes decreased from the center to the sides of cylinder radially. The grains sizes increased from the cylinder center to up and down surfaces axially as shown in Figure 7(b). The grain sizes of the sample with compressive strain rate of 0.01 s−1 were the smallest.Figure 7
The grain size distribution along radial (a) and axial (b) directions of the cylinder with different compressive strain rates.
(a)(b)


### 4.2. Mechanical Properties

True stress-strain curve of standard tensile samples was transformed by stress-strain curve obtained by using the universal testing machine GL8305. Figure8 illustrates that the tensile strength and fracture elongation of sample subjected to the compression deformation both increased in different degrees. The tensile strength and fracture elongation rate of the raw tensile sample are 516 MPa and 0.19. The improvement of tensile strength and fracture elongation of samples compressed with strain rate of 0.01 s−1 is the highest. Values of tensile strength and fracture elongation are 660.1 MPa and 0.26, which were increased by 28.1% and 35.3% compared to the raw sample. The tensile strength and fracture elongation of the sample compressed with the strain rate of 0.1 s−1 increased by 13.6% and 30.0%. The tensile strength and fracture elongation of the sample compressed with the strain rate of 1 s−1 increased by 10.1% and 10.0%.Figure 8
True stress-strain curve of standard tensile 7050 aluminium alloy samples.Tensile strength of the samples increased with the decrease of strain rate. Compression with smaller compress rate resulted in sufficient recrystallization and grain refinement. Refinement strengthening is an efficient way to improve mechanical properties of aluminium alloys, which was also reported in other works [20, 21]. Therefore, the improvement of the tensile strength of the compressed samples is mainly attributed to grain refinement, and this is in great agreement with the refinement degree of samples treated with different compressive strain rates.Figure9 shows the morphology of tensile fracture of the compression sample with different strain rates observed by SEM. It can be seen from Figure 9 that a large number of dimples were observed at the tensile fracture, indicating that 7050 aluminium alloy has good plasticity after thermal compression [22]. The dimples of the sample with strain rate of 0.01 s−1 were the largest and deepest. Small particles observed in the images were impurity precipitates. The dimples nucleated at the interface between the impurity precipitates and matrix grains and then grew up. Small dimples appeared at the edge of large dimples in the sample with strain rate of 0.1 s−1. The dimples were relatively shallow, and tearing ridges were formed on the fracture surface. The fracture morphologies of three specimens were in great agreement with the results of the tensile tests.Figure 9
Fracture images of samples compressed with strain rates of (a) 0.01 s−1, (b) 0.1 s−1, and (c) 1 s−1.


## 4.1. The Evolution of Microstructure

Figure2 shows the grain images oriented at the axial center of the cylindrical sample. Figures 2(a)–2(d) show the grain structure photographed by EBSD technique, and Figures 2(e)–2(h) show the simulated grain structure derived from the CA simulation technique. Figure 2(e) shows undeformed grains of raw aluminium alloy with mean sizes of ∼70 μm. The structures in Figures 2(b), (c) and (d) indicate that the grains of the compressed samples were refined after plastic deformation. As shown in Figure 2(b), coarse grains of samples loaded with a strain rate of 0.01 s−1 were crushed. A large number of fine grains appeared both inside the grains and near the grain boundary, which showed equiaxed shape. It reflects that dynamic recrystallization was fully finished in this sample. The microstructure of samples processed with strain rate of 0.1 s−1 at 350°C (Figure 2(c)) reveals that a lot of coarse grains were squeezed. A small number of fine grains appeared near the boundary of coarse grains, suggesting that dynamic recrystallization partially happened. In Figure 2(d), fine grains nucleated near the grain boundaries of most of the grains. It indicates that the dynamic recrystallization was about to happen. Table 3 shows the statistic of mean grain size derived from the EBSD and CA simulation method. The data of Table 3 and the insets in Figure 2 indicate that the mean grain sizes simulated by CA are consistent with the results of the images taken by EBSD. The deviation of mean grain sizes between two ways is smaller than 5%.Figure 2
The grain images in the axial center of the cylindrical samples compressed at 350°C with (a) no strain rate (raw structure); (b) compressive strain rate of 0.01 s−1; (c) compressive strain rate of 0.1 s−1; (d) compressive strain rate of 1.0 s−1. The CA simulated microstructure of samples compressed at 350°C with (e) no strain rate; (f) compressive strain rate of 0.01 s−1; (g) compressive strain rate of 0.1 s−1; (h) compressive strain rate of 1.0 s−1.Table 3
The mean grain size from EBSD and CA simulation.
Strain rate (mm/mm)Mean grain size (EBSD,μm)Mean grain size (CA,μm)Deviation (%)07070—0.0125.624.54.30.132.631.53.4144.842.64.9When the compressive rate is small, grain refinement in the alloy driven by the dynamic recrystallization mechanism can fully take place. The recrystallization process is attributed to sufficient degree of freedom for rotation and rearrangement of grain nuclei and subgrains [19]. When the compressive rate increases, there is low degree of freedom for rotation and rearrangement of grain nuclei and subgrains. High dislocation density-induced work hardening mechanism dominates the evolution of inner structure while there is not enough time to trigger the dynamic recrystallization of grains. In consequence, grains with small sizes are only formed around the grain boundaries in the samples compressed with high rate, as shown in Figure 2(d). The refinement of alloy grains can be realized by decreasing the compressive rate to improve dynamic recrystallization effect.Figure3 shows the grain size distribution along the axial and the radial directions of the sample loaded with compressive strain rate of 0.01 s−1 at 350°C. The strains and grain sizes of spots P1∼P7 are analyzed. The image of upper surface shows that the grains at the edge of the surface are the finest. The grain size increased from the edge to the center along the radial direction. The value increases from 2.38 μm to 50.3 μm. The axial change of grains indicates that the grain size increases from the cylinder center to both sides of the cylinder axially. This is because both sides of the sample were in contact with the punch and the die, respectively. The friction between the contact surfaces during plastic deformation obstructs the radial migration of atoms, which leads to the axial reduction of strain. The end face of the cylinder sample is a freely deformed surface with no obstruction of friction. Therefore, it migrates outside during the deformation. Furthermore, the local strain at the edge of upper and bottom surfaces of the sample also increased because of the “pull effect” from the end face of the cylinder. The strain distribution is shown by the coloured strain pattern of cylinder sample with strain rate of 0.01 s−1 at 350°C as shown in Figure 4. The sample in Figure 4 presents a bulge shape. The strain is the largest at the edge of the upper and bottom surfaces and at the center of the samples. The strain is the smallest at the center of the upper and bottom surfaces. The grain refinement is closely related to the strain distribution. The larger the strain is, the higher the grain refinement is.Figure 3
The grain size distribution of the cylinder sample with strain rate of 0.01 s−1 at 350°C.Figure 4
The coloured strain pattern of the cylinder sample with strain rate of 0.01 s−1 at 350°C.Figure5 shows the curve of strain vs. deformation time of the sample with compressive strain rate of 0.01 s−1 at 350°C. Data of spots P1–P5 marked in Figure 5 were collected. The strain of P1 is 1.78 which is the largest of the alloy after deformation. The largest strain value of P4 after deformation is 1.64. The strains of P2, P3, and P5 show a similar curve as shown in Figure 5. Figure 6 shows the strain distribution along the axial and radial directions. The radial direction takes the center of the circle on the upper surface as the origin point, and the axial direction takes the center of the cylinder as the origin point. The radial curve indicated that the strain of about 80% of spots kept a value of ∼0.5 mm/mm. The strain along the axial direction decreases from the center to both sides evenly.Figure 5
Curve of strain vs. deformation time of spots derived from Figure4 (P1∼P5).Figure 6
Strain deformation along axial and radial directions of the cylinder.Figure7 shows the grain size distribution along axial (Figure 7(a)) and radial (Figure 7(b)) directions with different compressive strain rates. The distribution of grain sizes is in great agreement with distribution of strain. As shown in Figure 7(a), the grain sizes decreased from the center to the sides of cylinder radially. The grains sizes increased from the cylinder center to up and down surfaces axially as shown in Figure 7(b). The grain sizes of the sample with compressive strain rate of 0.01 s−1 were the smallest.Figure 7
The grain size distribution along radial (a) and axial (b) directions of the cylinder with different compressive strain rates.
(a)(b)


## 4.2. Mechanical Properties

True stress-strain curve of standard tensile samples was transformed by stress-strain curve obtained by using the universal testing machine GL8305. Figure8 illustrates that the tensile strength and fracture elongation of sample subjected to the compression deformation both increased in different degrees. The tensile strength and fracture elongation rate of the raw tensile sample are 516 MPa and 0.19. The improvement of tensile strength and fracture elongation of samples compressed with strain rate of 0.01 s−1 is the highest. Values of tensile strength and fracture elongation are 660.1 MPa and 0.26, which were increased by 28.1% and 35.3% compared to the raw sample. The tensile strength and fracture elongation of the sample compressed with the strain rate of 0.1 s−1 increased by 13.6% and 30.0%. The tensile strength and fracture elongation of the sample compressed with the strain rate of 1 s−1 increased by 10.1% and 10.0%.Figure 8
True stress-strain curve of standard tensile 7050 aluminium alloy samples.Tensile strength of the samples increased with the decrease of strain rate. Compression with smaller compress rate resulted in sufficient recrystallization and grain refinement. Refinement strengthening is an efficient way to improve mechanical properties of aluminium alloys, which was also reported in other works [20, 21]. Therefore, the improvement of the tensile strength of the compressed samples is mainly attributed to grain refinement, and this is in great agreement with the refinement degree of samples treated with different compressive strain rates.Figure9 shows the morphology of tensile fracture of the compression sample with different strain rates observed by SEM. It can be seen from Figure 9 that a large number of dimples were observed at the tensile fracture, indicating that 7050 aluminium alloy has good plasticity after thermal compression [22]. The dimples of the sample with strain rate of 0.01 s−1 were the largest and deepest. Small particles observed in the images were impurity precipitates. The dimples nucleated at the interface between the impurity precipitates and matrix grains and then grew up. Small dimples appeared at the edge of large dimples in the sample with strain rate of 0.1 s−1. The dimples were relatively shallow, and tearing ridges were formed on the fracture surface. The fracture morphologies of three specimens were in great agreement with the results of the tensile tests.Figure 9
Fracture images of samples compressed with strain rates of (a) 0.01 s−1, (b) 0.1 s−1, and (c) 1 s−1.


## 5. Conclusion

7050 aluminium alloy cylinder samples with size of Ф80 mm × 100 mm were isothermally compressed with three strain rates (0.01 s−1, 0.1 s−1, and 1 s−1) at 350°C. The cylinder samples were processed to standard tensile specimens at room temperature. Tensile testing was done by using the GL8305 universal testing machine. The grain evolution and fracture morphology were analyzed by the CA simulation method and SEM observation. The effect of compressive strain rate on alloy microstructure and mechanical properties was investigated. For 7050 aluminium alloy, the following conclusions can be drawn:(1)
Grain refinement occurred during the compression deformation of 7050 aluminium alloy. The sample with strain rate of 0.01 s−1 achieved the smallest grain size. The analysis of sample with strain rate of 0.01 s−1 reveals that the grain size decreased radially from the center of the upper surface. The grain size increased axially from the center of the cylinder to both sides.(2)
The tensile strength and fracture elongation of 7050 aluminium alloy were improved after compressive deformation. The tensile strength and fracture elongation of sample with strain rate of 0.01 s−1 increased to 660 MPa and 0.26, which increased by 28.1% and 35.3%.(3)
Dimples were formed on the fracture section. Dimples on the fracture section of samples with strain rate of 0.01 s−1 were the largest and the deepest.



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