The Mechanical Properties of Atomic Layer Deposited Alumina for Use in Mems and NemsTripp2006
Mechanical and Physical Properties of Micro Alumina ...
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International Journal of Mechanical & Mechatronics Engineering IJMME-IJENS Vol:20 No:03 32
201003-4747-IJMME-IJENS © June 2020 IJENS I J E N S
Mechanical and Physical Properties of Micro
Alumina Reinforced Direct Recycled AA6061
Chips Based Matrix by Hot Extrusion Process
H. M. Sabbar 1,a, Z. Leman1,2,b*, Mohammed H. Rady3,c, S. Shamsudin4,d,
Suraya Mohd Tahir1,e, C. N. Aiza Jaafar1,f , MA Azmah Hanim1,g, Nur Ismarrubie Zahari1,h and M. S.
Msebawi 1,i.
1Department of Mechanical and Manufacturing Engineering, Faculty of Engineering, Universiti Putra Malaysia, 43400 Serdang, Selangor, MALAYSIA.
2Advanced Engineering Materials and Composites Research Centre, Faculty of Engineering, Universiti Putra Malaysia,
43400 Serdang, Selangor, MALAYSIA. 3College of Engineering, Wasit University, Iraq
4Faculty of Mechanical and Manufacturing Engineering, Universiti Tun Hussein Onn Malaysia, Batu Pahat, Johor,
Malaysia [email protected], [email protected], [email protected] [email protected],
[email protected], [email protected], [email protected], [email protected], [email protected].
Abstract-- Direct hot extrusion is an alternative process for
recycling aluminium without melting the scrap. It utilizes low
energy and is environmental friendly. This study shows the
effects of preheating temperature (PHT), preheating time
(PHti) and addition of volume fraction (VF) of micro alumina
on the microhardness (MH), density and microstructure of
the extruded profiles. Three values of PHT (450, 500, 550 °C),
PHti (1, 2, 3 hours) and VF (5, 10, 15 %) were considered
respectively. The full factorial design with center point
analysis was used to demonstrate the effect of process
variables on responses. A total of 19 experimental runs were
performed through the hot extrusion process. The results
show that the preheating temperature is the most important
factor to be controlled in order to obtain the optimum MH
and density, while preheating time and volume fraction
trailed behind the former. It can be concluded that
microhardness increases with the increase in PHT and
decrease in PHti and VF. On the contrary, an increase in
density was observed with a decrease in PHT, PHti and VF
apiece. The impact of hot extrusion parameters on the average
grain sizes and microstructural analysis of the recycled
samples were equally investigated and discussed. Index Term-- AA6061, Aluminum Alloy, Density, Hot
Extrusion, Micro Alumina, Microhardness, Metal Matrix
Composites, Microstructure.
1 INTRODUCTION
Recycling of aluminium alloy scraps is often done by conventional re-melting where part of the material is recovered and another part is lost to the processes of the production [1] in addition to the high energy demand and environmental pollution [2]. Because of these reasons, nowadays, there are delibrate efforts aimed at reducing energy consumption and environmental conservation by using economically viable methods instead of conventional recycling. This method is known as the direct treatment of alloy chips, called solid-state recycling [3,4]. It was suggested to be a good alternative to conventional recycling and offers a green process, hence
employing the plastic deformation technique. The solid-
state recycling converts the metal scraps into bulk material,
contrary to the conventional energy intensive technique [5-
7]. The hot extrusion process could not only conserve the
environment but equally eradicate the generation of new waste [8].
The physical, mechanical properties and
microstructure of products extruded using the solid-state
recycling of aluminum alloy chips are controlled by a
number of the hot extrusion parameters. Previous studies
had reported temperature related parameters, extrusion
ratio, die geometry, chip morphology and ram speed to be
among the relevant factors worthy of understudying in
order to obtain qualitative products from the direct
recycling process [9, 10]. This study focuses on the effects
of preheating temperature, preheating time and volume fraction on the resulting mechanical and physical
properties of micro alumina reinforced aluminum chips
based matrix composite. The influence of each factor was
analyzed using the Analysis of Variance (ANOVA) of full
factorial design. This work also investigates the analysis of
microstructure and the average grain sizes of the
extrudates.
2 WORKING PROCEDURES
2.1 Preparing the samples
The main raw material used in this study is a block
AA6061 aluminium alloy from which chips was prepared.
The high-speed milling technique was used in chips preperation. The choice of the high-speed milling was
owing to its ability to produce chips that have comparable
properties with the aluminium alloy. Previous studies
reported that this technique have no deformability on the
mechanical properties of recycled materials [8, 11]. The
dimensions of the examined chip particles were 3.40-3.70
mm length × 1.630 mm width × 0.094 mm thickness with
12.35 mm2 surface area per chip. The mechanical
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properties of the aluminum alloy AA6061 used in this study
are summarized in Table 1. Table I
Range of mechanical and physical properties of AA6061-T6 [12]
Properties Value (data obtained at temperature =25 °C)
Max. Min.
Density (g/cm3) 2.70 2.66
Tensile strength (MPa) 319 315
Yield strength (MPa) 292 291
Elongation (%) 13 12
In order to remove stains and impurities in the form of
drop of oil that might have stitch with the aluminium alloy
chips, the ASTM G131-96 was adopted in cleaning the
chips. The ultrasonic methods was used during the cleaning
operations. After cleaning the chips, the aluminuim was
mixed with micro alumina using the 3D mixer. The mixture
was compressed into a cylindrical die using cold press to produce billets of approximately 90 mm length x Ø30 mm.
The order used in conducting the experiment is presented
in Fig. 1. Additional conditions used during the extrusion
of the billets is presented in Table 2. Key among the
parameters varied are the preheating temperature, time and
volume fraction of alumina. The order of variation were
450 - 550 °C, 1 – 3 hours and 5 - 15%, apiece. In order to
avoid the formation of hot cracks, the highest preheating
temperature was limited to 550 °C. Previous study had
reported that the surface of extruded products at a
temperature higher than 550 °C had cracks [12]. A ceramic
heater was used in generating the required heat. The heater was fixed around the container. Graphite-based lubricant
was used on the inner surface of the die and container at
every extrusion cycle to prevent increase in the load of
extrusion due to friction.
Fig. 1. Process sequence of experimental work
Table II
Parameter used during the hot extrusion process of the billets
Parameter Value/type
Geometry/ shape of the die Round
Ratio used in extrusion, R 5.4
Diameter of billet, Ø (mm) 30
Speed of extrusion, s (mm/s) 1
Container temp, Tcont (°C ) 300
Die temp., Tdie (°C) 300
Preheating temp., Tph (°C) 450, 500, 550
Preheating time, tph (hr) 1, 2, 3
Volume fraction (Al2O3), Vf (%) 5%, 10%, 15%
2.2 Test methods
Microhardness test was done using a load of 0.9807 N
and 10 seconds as holding time for the test at room
temperature. The hardness test was carried out using the
Micro Vickers hardness machine, following the grinding of
the surfaces of each sample in order to obtain a balanced
indentation. A square base pyramid formed diamond was
utilized for testing in the Vickers scale. Three places (top,
center, and bottom) of the samples were indented, out of
which the average was taken as the hardness value for each
sample.
Sample preparation for density was done by obtaining circular pieces sectioned to a dimension of
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approximately 1 mm in diameter and thickness. The HR-250AZ- Compact Analytical Balance density determination kit was used for this purpose. Density test was done using the Archimedes’ water immersion principle. The small pieces of specimens were weighted in air and distilled water to record the weight in different
environments. Each sample was immersed in distilled water during the density measurement. The room temperature was recorded to calculate the density of the
composite material based on the following formula:
𝐷𝑒𝑛𝑠𝑖𝑡𝑦 = 𝐴
│𝐵│ × 𝑑𝑒𝑛𝑠𝑖𝑡𝑦 𝑜𝑓 𝑑𝑖𝑠𝑡𝑖𝑙𝑙𝑒𝑑 𝑤𝑎𝑡𝑒𝑟
(1) Where,
A = 𝑤𝑒𝑖𝑔ℎ𝑡 𝑜𝑛 𝑎𝑖𝑟
B = 𝑤𝑒𝑖𝑔ℎ𝑡 𝑖𝑛 𝑙𝑖𝑞𝑢𝑖𝑑
2.3 Experimental Design
A 23 full factorial with 2 replicates was adopted in
conducting the experiment. Parameters were varied in
accordance with each run. The choice of this 2 replicates
was to enable an analysis of the variation in parameters to
be conducted. The variation followed the three enumerated
process parameters. Three center points were included in
the factorial design to investigate the curvature effect. This
would further suggest whether the linear model was
sufficient to define the relationship between process factors
over response or vice versa. The interactions between factors were also investigated. The selected parameters
with their levels in factorial design are shown in Table 3.
Two runs were carried out in each corner, a combination of
which resulted in 19 experimental runs, herein referred to
as S1-S19. Table 4 is a representation of the full layout of
the planned experiment based on the design of experiment
(DOE). The focus of the study were represented by the
responses which are the microhardness and density of the
fabricated samples. In order to identify the key factor(s)
effecting on the properties measured, the Analysis of
variance (ANOVA) was deployed. The process was also
relevant in analysing the relationship between the input parameters. The results of ANOVA in the factorial design
can give a further insight into the experimental direction for
process optimization.
Table III
Outline of design and experimental process parameters, including levels
Parameter
symbol Parameter
Levels
Low (-1) Center (0) High (+1)
A Preheating temperature, (PHT) 450 500 550
B Preheating time (PHti) 1 2 3
C Volume fraction (VF) 5% 10% 15%
3 RESULTS AND DISCUSSION
The full factorial design with three center points were deployed as a guide for conducting the total nineteen
experimental runs. The results of the experiments are tabulated in Table 4. The result revealed that higher microhardness
were obtained from samples extruded using the maximum PHT and the minimum VF. On the other hand, a rise in density
was observed from samples extruded using minimum PHT, PHti and VF. Further discussions are made in the subsequent
sections to clarify the ANOVA findings of the factorial design.
Table IV
Results of microhardness and density, showing the effect of PHT, Phti and VF on both properties
Sample
Designation
PHT(A)
(°C )
PHti(B)
(hr)
VF(C)
(%)
Microhardness
(MH)
(HV)
Density
Analysis
(g/cm3)
S1 450 1 5 43 2.70
S2 550 1 5 53 2.57
S3 450 3 5 45 2.65
S4 550 3 5 55 2.53
S5 450 1 15 46 2.68
S6 550 1 15 57 2.56
S7 450 3 15 48 2.60
S8 550 3 15 50 2.50
S9 450 1 5 40 2.73
S10 550 1 5 61 2.57
S11 450 3 5 49 2.64
S12 550 3 5 56 2.51
S13 450 1 15 48 2.69
S14 550 1 15 52 2.55
S15 450 3 15 47 2.58
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S16 550 3 15 50 2.49
S17 500 2 10 52 2.61
S18 500 2 10 61 2.59
S19 500 2 10 58 2.58
3.1 ANOVA Results of Microhardness
The result of microhardness revealed that samples
extruded using high preheating temperature had higher
hardness values as against their counterpart extruded at low
preheating temperature. This was a clear indication that the
microhardness was sensitive to the extrusion preheating
temperature. For clarifications, when billets are extruded at
higher preheating temperature and low volume fraction of
alumina, an efficient consolidate of the aluminium alloy
chips and alumina was better due to increase in the
bounding mechanism within the composite. The same reason was responsible for the increase in microhardness of
samples S10, S18 and S19. The implication was that at high
temperature, matters are diffused faster in accordance with
the transportation of natter principles, hence resulting to
better chips bonding. The same reason was responsible for
the voids free and compacted microstructure. The fine grain
sizes observed in these composites was in concurrent with
the hard surface texture observed in the samples extruded
using high preheating temperature.
Output of the ANOVA depicts that the relevant
factors effecting on the microhardness of the aluminium
matrix composite fabricated using the hot extrusion process
is only the preheating temperature. The p < 0.05 was a clear
indication of the effect of the factor as presented in Table 5
and further clarified by the Pareto Chart in Fig. 2. Other parameters like, preheating time (B), volume fraction (C),
the interaction of PHT and PHti (A*B) and the interaction
of PHT, PHti and VF (A*B*C) were of less significant
towards microhardness.
Table V
ANOVA results of factorial design for microhardness
Source DF Adj SS Adj MS F-Value P-Value
Model 7 390.898 55.843 2.74 0.066
Linear 3 288.372 96.124 4.72 0.024
PHT 1 287.252 287.252 14.10 0.003
PHti 1 0.345 0.345 0.02 0.899
VF 1 0.776 0.776 0.04 0.849
2-Way
Interactions 3 101.812 33.937 1.67 0.231
PHT*PHti 1 35.745 35.745 1.75 0.212
PHT*VF 1 50.719 50.719 2.49 0.143
PHti*VF 1 15.348 15.348 0.75 0.404
3-Way
Interactions 1 0.714 0.714 0.04 0.855
PHT*PHti*VF 1 0.714 0.714 0.04 0.855
Error 11 224.058 20.369
Pure Error 10 89.776 8.978
Total 18
Fig. 2. Pareto chart for microhardness
The implication of this result was that specimen
fabricated using higher preheating temperature may result
in higher microhardness. Increasing the temperature to 550
°C and decreasing the volume fraction to 5% will increase
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the microhardness to the maximum level. Furthermore, the
samples extruded at 450 °C and 15% volume fraction of
alumina resulting in the least hardness performance. In
ANOVA analysis, the main effect plot as presented in Fig.
3 clearly shows that all the center points lie very close to
the linear lines of the average microhardness. In addition, they are connected from low to high setting of preheating
temperature, preheating time and volume fraction
parameters.
Apparently, the interaction plot as shown in Fig. 4
exhibits a similar trend to the main effect plot. This
indicates that all the observed data are accurately plotted
according to the ANOVA results. Besides, the curvature
effect was insignificant on the response. Mentioned here
was that the insignificancy of carvature was in agreement with the ANOVA report presented in Table 6. The
observed p > 0.05 showed that the linear model was
sufficient in fitting all the data. This p value was a
demonstration of the curvature term.
Fig. 3. Main effects plot for microhardness
Fig. 4. Interaction plot for microhardness
The response optimizer approach was used to further optimise the parameter settings. This allows the maximum
microhardness to be obtained with the least trials, which is an important consideration for the economic scale of
production. Fig. 5 shows the response optimizer analysis for microhardness which revealed that 58HV was the optimum
hardness obtainable at 550 °C, 1 hours and 5% volume fraction of alumina conditions.
Fig. 5. Optimization plot for microhardness
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3.2 ANOVA Results for Density
The ANOVA conducted in respect of density
indicated that the value of density increased with decrease
in all the parameters used in extruding samples. Therefore,
it was noted the maximum value of density was at 450 Ċ, 1
hour and 5 % for PHT, PHti and VF respectively. The implication of this result was that the chips were compacted
to be outrageously dense which resulted in poor inter-chip
consolidation. It is therefore clear that stress was higher on
the samples when PHT, PHti and VF were low. By
extension, these conditions of extrusion were only suitable
at eliminating the voids, but incapable of improving the
chip bonding. Previous study had reported higher strength
in samples extruded using high temperature [13]. However,
such conditions resulted in lower density because the
extruded products encountered residual voids and cracks.
This indicates that the preheating temperature is the most
influential factors towards density in solid-state recycling method using hot extrusion process.
The ANOVA results indicate that all parameters
PHT, PHti and VF were significant terms contributing to
the density of hot extruded aluminium matrix composite.
However, the p < 0.05 for preheating temperature was a
more influential factor towards the density as against the
preheating time and volume fraction of alumina. The result presented in Table 6 and Pareto Chart in Fig. 6 clearly
indicated the aforementioned relationships. For
clarifications, the interaction between preheating
temperature and preheating time, preheating temperature
and volume fraction were not significant towards the
density of the samples herein reported. Furthermore, the
relationship between PHT, PHti and VF were equally not
significant towards density. Figs. 7 and 8 present the main
effect plot and interaction plot apiece. The main effect plot
indicates that PHT and PHti were the significant parameter
effecting on the response. It should be noted also that the
interaction plot followed a similar trend with the main effect plot and the curvature effect was unimportant.
Table VI
ANOVA results of factorial design for density
Fig. 6. Pareto chart for density
Source DF Adj SS Adj MS F-Value P-Value
Model 8 0.085725 0.010716 70.65 0.000
Linear 3 0.084069 0.028023 184.77 0.000
PHT 1 0.061256 0.061256 403.89 0.000
PHti 1 0.018906 0.018906 124.66 0.000
VF 1 0.003906 0.003906 25.76 0.000
2-Way Interactions 3 0.001569 0.000523 3.45 0.060
PHT*PHti 1 0.000756 0.000756 4.99 0.050
PHT*VF 1 0.000506 0.000506 3.34 0.098
PHti*VF 1 0.000306 0.000306 2.02 0.186
3-Way Interactions 1 0.000056 0.000056 0.37 0.556
PHT*PHti*VF 1 0.000056 0.000056 0.37 0.556
Curvature 1 0.000032 0.000032 0.21 0.657
Error 10 0.001517 0.000152
Total 18 0.087242
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Fig. 7. Main effects plot for density
Fig. 8. Interaction plot for density
In order to independently investigate the effect of each parameter on the response individually, the response
optimizer method was adopted. The aim was to evaluate their impact on the extruded product in terms of density. The
response optimizer has the capability of revealing the optimum parameter required to obtain the maximum response. Figs.
9 represent the analysis of optimizer response from Design of Experiment for density.
Fig. 9. Optimization plot for density
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3.3 Microstructure investigation
Microstructural investigation of mechanically
grinded, ploished and atched cupons were conducted on the
optical microscope (OM). SiC grits paper of 240, 600, and
1200 grades were used in grinding the samples for 3
miniutes each under the flow of water. This was followed by polishing using colloidal silica. The polished samples
were etched utilizing Barker’s reagent with a voltage of U
= 12 Volt DC for 2 miniutes. ASTM E112-13 standard was
adopted in measurement of grain sizes, in accodance with
the mean linear intercept procedure.
The microstructural analysis of the extrudates
processed at different preheating temperatures, time and
volume fraction of alumina revealed grains with differed
sizes as shown in Fig.10. For instance, fine grains can be
observed in the microstructure of the samples preheated at
450 °C, 15% Al2O3 . These grains were as a result of the
dynamic recrystallization during the hot extrusion. Further observed in the composites fabricated using the
aforementioned parameters were smaller grain sizes and
chip boundaries with no voids and visible cracks.
At the above condition, when preheating times
were 1 hour and 3 hours, the average grain size were 22.35
μm and 21.74 μm respectively. A decrease in the volume
fraction of alumina from 15 % to 5 %, while other
parameters were maintained as above resulted to an
increase in the average grain sizes of 34.82 μm and 32.44
μm. This indicates that particle sizes of alumina effected
on microstructure of extrudates. When preheating
temperature was increased to 500 °C and the volume
fraction of alumina was decreased to 10 %, the
unrecognized and non-uniform shapes were observed in
case of the new microstructure. Smooth boundary lines and
voids can be observed, while the composites contained a very dense microstructure. With this condition, the
measurement of grain size increased to 41.26 μm.
At 550 °C and 5% alumina, the shape of grains
become more equiaxed and recrystallized. That was an
indication that the grain coarsening had occurred at this
processing temperature. The same reason was responsible
for the increase in the average grain size which reached a
maximum value of 47.61 μm at 3 hours. When 550 °C
preheating temperature and 15 % volume fraction of
alumina was used, the grain size measurement decreased to
29.52 μm at 3 hours as shown in Table 7. These findings
are in agreement with the literature [14]. From this result, it is clear that increase in the
temperature increased the grain size of recycled chips.
However, the growth of the grain can be avoided by the
presence of the Al2O3 reinforcement particles which act as
obstacle to the grain boundary movements [15]. The
analysis of grain structure showed that fine and suitable
average grain sizes and smooth boundary lines were
beneficial to high tensile strength. This was in combination
with high preheating temperature and low volume fraction
of alumina. The duo could efficiently consolidate the
composite during the extrusion process.
Table VII
Grain size measurement
Sample No.
Parameter Condition
G No. Average diameter
(µm) PHT(A)
(°C )
PHti(B)
(hr)
VF(C)
(%)
S1 450 1 5 6.12 34.82
S2 550 1 5 4.70 45.27
S3 450 3 5 6.55 32.44
S4 550 3 5 4.46 47.61
S5 450 1 15 9.51 22.35
S6 550 1 15 6.68 31.83
S7 450 3 15 9.79 21.74
S8 550 3 15 7.21 29.52
S19 500 2 10 5.15 41.26
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Fig. 7. Microstructure of extrudate produced at different PHT, PHti and VF: (a) 450 °C, 1 hour and 15%; (b) 450 °C, 1 hours and 5%; (c) 500 °C, 2
hours and 10%; (d) 550 °C, 3 hours and 15%; (e) 550 °C, 3 hours and 5%.
CONCLUSION
The focus of this study was to conduct a
comprehensive investigation and computational analysis of
the effects of preheating temperature (PHT), preheating
time (PHti) and volume fraction (VF) of alumina on the
microhardness, density and microstructure of AA6061
composite reinforced with micro alumina. It was clear from
the ANOVA that the main factor that was significant to the
microhardness was the PHT. On the other hand, PHti and
VF were not significant. Here, with PHT at 550 oC, PHti at
1 hour and VF at 5 %, the maximum hardness of 61 HV
and a density of 2.57 g/cm3 were obtained. On the other
hand, all the factors PHT, PHti and VF were considering as
significant factors effecting on the density of the
composite. The microhardness was sensitive to the
extrusion preheating temperature because the extrusion
process done at high billet temperature efficiently
consolidated the material. The highest density 2.73 g/cm3
was obtained at a PHT of 450 oC, PHti of 1 hour and VF of
5%, when hardness was 40 HV. Density was high at low
PHT, PHti and VF because the compression pressure and
extrusion stress produced at these conditions were only
sufficient at eliminating the voids which led to the increase
in density, but was incapable of improving chip welding.
ACKNOWLEDGMENTS
This research was financially supported by the Research
Management Centre, Universiti Putra Malaysia for support
of this research work. The first author thanks the School of
Graduate Studies, for financial support to study at
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Universiti Putra Malaysia. We acknowledge the use of
facilities within the Centre for Graduate Studies, Universiti
Tun Hussein Onn Malaysia (UTHM) and Sustainable
Manufacturing and Recycling Technology, Advanced
Manufacturing and Materials Center (SMART-AMMC),
Universiti Tun Hussein Onn Malaysia (UTHM). We equally acknowledge the College of Engineering, Wasit
University, Iraq for research collaborations.
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