Published at : 28 Jul 2023
Volume : IJtech
Vol 14, No 5 (2023)
DOI : https://doi.org/10.14716/ijtech.v14i5.6032
Yahya M. Altharan | Sustainable Manufacturing and Recycling Technology, Advanced Manufacturing and Materials Center (SMART?AMMC), Universiti Tun Hussein Onn Malaysia, Parit Raja 86400, Malaysia |
S Shamsudin | Sustainable Manufacturing and Recycling Technology, Advanced Manufacturing and Materials Center (SMART?AMMC), Universiti Tun Hussein Onn Malaysia, Parit Raja 86400, Malaysia |
Sam. Al-Alimi | Sustainable Manufacturing and Recycling Technology, Advanced Manufacturing and Materials Center (SMART?AMMC), Universiti Tun Hussein Onn Malaysia, Parit Raja 86400, Malaysia |
Mohammed A. Jubair | Department of Computer Technical Engineering, College of Information Technology, Imam Ja'afar Al-Sadiq University, 66002 Al-Muthanna, Iraq |
The solid-state recycling technique has gained significant
attention for its ability to reduce metal losses, energy consumption, and solid
waste. This study introduced solid-state recycling method to develop zirconia-reinforced
AA7075/AA7050 aluminum chip-based matrix composite via a hot press forging
process (HPF). The chips were cold-compacted at 35 tons and then hot-forged
through a dog bone-shaped die. Full factorial and response surface methodology
(RSM) designs were applied using Minitab 18 software. The Face Centred
Composite (CCF) of RSM was adopted to rank each factor's effect and analyze
interactions between input factors and output responses, followed by process
optimization. The selected factors of temperature (Tp) and volume fraction of
zirconia (ZrO2) nanoparticles (Vf) were set at 450, 500, and 550 °C
with 5, 10, and 15 wt %, respectively. The analyzed responses were ultimate
tensile strength (UTS) and microhardness (MH). SEM micrograph revealed a slightly
uniform distribution of ZrO2 particles in the matrix. The developed
composite gained the maximum strength of 262.52 MPa, a microhardness of 135.5
HV and a density of 2.828 g/cm3 at 550 °C and 10 wt % setting. RSM
optimization results suggested 550 °C and 10.15 wt % as optimal conditions
for maximum UTS and MH. The preheating temperature exhibited a more
significant influence than the ZrO2 volume fraction on the
composite's mechanical properties; however, both had a slight effect on grain
size. The future prospects of this work are briefly addressed at the end. In
conclusion, the HPF process was found to be an efficient recycling method for
mitigating environmental impacts by conserving energy and materials.
Composite, Mechanical properties, Microstructure, Recycling
Aluminum alloys are the most commonly used materials
in automotive and aerospace structures due to their lightweight properties and
enhanced fuel efficiency to reduce CO2 emissions
and 40% come from the aluminum production processes. Primary
aluminum production (mining from bauxite ore) requires 113 GJ of energy
per tonne, while secondary production (recycling) needs just 13.6 GJ per tonne
The considerable amounts of scrap and chips
generated during machining are able to be recycled and repurposed to achieve
sustainability. Numerous researchers have studied aluminum waste recycling to
save energy and reduce environmental issues (Yong et al., 2019; Keoleian
and Sullivan, 2012). However,
recycling aluminum by remelting still consumes high energy and emits CO2,
according to some studies
In the current research, AA7075/AA7050 chip
was recycled through HPF and reinforced by zirconia particles (ZrO2)
with an average size of ZrO2-nanoparticle was chosen due to
its mechanical properties, high-temperature stability, wear, corrosion, and
chemical resistance
This
research aims to recycle AA7075/AA7050 aluminum chip by HPF and investigate the
influence of preheating temperatures and ZrO2 addition on the
mechanical and physical properties of the forged composite. The developed
composite material was able to be used in the transportation industry. However, the profile quality is able to be
improved by heat treatment. This research has a tendency to contribute to
further attention toward direct recycling technologies to conserve energy and
natural resources.
2.1. Materials
preparation
The materials used, such as aluminum
chips and zirconia reinforcement material, were supplied by SMART-AMMC, UTHM.
The chips were produced from AA7075/AA7050 aluminum bulk with 3.30 × 1.12 ×
0.095 mm average size using Sodick-MC430L high-speed milling. The chip was
cleaned using acetone (C3H6O) in an ultrasonic bath based on ASTM G131-96 and
then dried at 60 °C for 30 min. The prepared chips were mixed with zirconia
nanoparticles averaging in size using a 3D mixer.
2.2. Rule of mixing
The aluminum chip and reinforcement
particles were mixed to develop uniform distribution throughout the composite.
The density-based mixtures rule method was used to determine the required
amount of chips and zirconia nanoparticles for the composite production, as
presented in the following equations:
Where is composite’s density, V
refers to volume with subscripts z and m for zirconia nanoparticles and metal
matrix, respectively.
Where Vf is the volume fraction of
particles. Mm and are mass and density of the particles and
matrix, respectively.
2.3. Experimental
design
Design of experiments (DOE) was used to determine
the influence of significant factors and their interactions to optimize the
responses via RSM. The input factors were temperature (Tp: 450, 500, and 550
°C) and ZrO2 (Vf: 5, 10, and 15 wt %). The UTS and MH responses of
the forged composite were investigated by varying the input factors. To analyze
the influence of different settings of Tp and Vf on UTS and MH, the 2k
full factorial design (k is number of factors) with 2 replicates and 3 center
points for curvature effect analysis was chosen as it is very useful in
screening the significant factors of the experiment. Eleven runs were involved,
corresponding to the experimental design selected and the run scheme given in
Table 1. The star points correspond to value of 1 to evaluate the interaction
between the parameters. RSM was used to obtain the optimal setting that
resulted in the highest UTS and MH. The model's regression general equation (6)
determines the correlation between the dependent (responses) and independent
variables (input factors).
2.1.
Hot Press
Forging process (HPF)
The mixture of chip and ZrO2 particles was weighed at 14 g
as per the rule of mixing result and filled up into Flat-Face dog bone-shaped
die in Figure 1(a), then cold compacted at 35 tons and four times
pre-compacting cycle. The billet die was preheated for 45 min of homogenization
time at the desired temperature followed by 2 hours of holding time and forging
temperatures (Tp) of 450–550 °C, between the solidus and recrystallization
point.
Figure 1 (a) Top and bottom forging
die, (b) Forging machine, (c) Tensile testing machine, (d) Forged specimens,
(e) Hardness tester and (f) SEM microscope
2.1. Experimental
Tests
The exact geometric dimensions of specimens were
based on ASTM E8/E8M (Figure 2). The
tensile test of samples was performed using a universal testing machine
(Shimadzu EHF-EM0100K1-020-0A). The hardness specimens were tested by Vickers
microhardness tester, under a predetermined force of 2.943 N load for 10 s
(ASTM E384-11). Microstructure tests were conducted utilizing a scanning
electron microscope SEM-JSM T330. The fracture surface morphology was examined
by SEM Hitachi SU1510 based on Standard ASTM E3 and ASTM E340 through an
optical microscope (Olympus BX60M). The testing specimens were ground using
240, 600, and 1200 SiC paper for 3 min, polished to 6 µm TEXPAN, 1 and 2 µm
NAPPAD for 540 s each, then etched at 12 V DC for 2 minutes by Barker's
reagent. The density test was carried out in distilled water for whole
specimens using HR-250AZ-Compact Analytical Balance Density Determination Kit.
Small billet specimens were weighed in air and distilled water to record the
weight in various environments. The room temperature was recorded to calculate
the relative density by using the following equation:
Where m, and V are density,
mass on air, and volume in liquid, respectively
Figure
2 Plate-type Tension Test Specimen (ASTM E8M)
Table 2 The chemical composition of AA7075/7075 (ASTM
B221M -13, 2015,354)
3.1. Ultimate tensile strength (UTS)
The
UTS results with different temperatures and ZrO2 volume fractions,
including four additional experiments suggested by DOE for process optimization are shown in Table 3. UTS increased by 288.13% from 56.94 to 221
MPa for 550 °C-forged samples (S1) and 450 °C-forged samples (S2), despite both
two samples being reinforced by 5 wt % ZrO2 particles. The UTS of S2
and S13 embedded with 5 and 10 wt % and 550 °C-forged increased by18.78% from
221 MPa to 262.52 MPa. The composite's dislocation density exceeded that of the
zirconium oxide nanoparticles. In metal deformation, the strength increases
linearly with dislocation density
The
findings show that the UTS was high at 550 °C with different wt % of ZrO2.
The higher operating temperature above the solidus point resulted in good
metallic bonding between consolidated chips. High processing temperature and
average weight content of ZrO2 resulted in relatively recrystallized
grains, where grain coarsening was metallurgically bonded
Table 3 Results
of Elongation at Break, Yield strength, UTS, and MH tests for all samples
3.2. Microhardness
Microhardness
results at different operating temperatures and ZrO2 volume
fractions are listed in Table 3. The
highest value of hardness was observed at 550 °C and 10 wt % of ZrO2.
With 5 wt % ZrO2 addition and forging temperatures of 450 and 550
°C, hardness increased by 38.42% (S1 and S2). However, the hardness of S12 and
S13 forged at 450 to 550 °C increased by 54.7% from 87.6 to 135.5 HV with 10 wt
% ZrO2 addition.
As
shown in Table 3, the MH of the 100% chip sample (S16) was 98.03 HV, whereas
the sample reinforced with 10 wt % ZrO2 (S13) had the highest MH of
135.50 HV. The hardness increment was 38%, although both two samples (S13 and
S16) were preheated at 550 °C. Sample S13 recorded the highest hardness of
135.5 HV, presenting the considerable effect of 10 wt % of ZrO2
particles and 550 °C forging temperature. This result corresponds to the trend
observed in the UTS results. Moreover, it has been demonstrated that increasing
temperature above 500 °C contributed to increased strength due to finer
particle dispersion
3.3. Modelling and optimization of
the experimental factors for MMC performance
3.3.1
ANOVA of ultimate tensile strength and microhardness using RSM
The obtained UTS and MH data were used for
further analyses by ANOVA and regression analysis. ANOVA and RSM were carried out to determine the significance of each
factor considered in the experiment. The ANOVA results of the full factorial
and curvature test suggested further optimization due to the positive effect of
curvature. Therefore, four more experiments were added.
In UTS result analysis, R2,
adjusted R2, and predicted R2 have
respective values of 0.9902, 0.9863, and 0.9769. The results prove the impact
of zirconia particles on the TS of the developed composite. Meanwhile, the R2,
adjusted R2, and predicted R2 values for MH
are 0.967, 0.949, and 0.8985, respectively (refer to Table 5). The R2
value of 0.967 is close to 1, which explains the strong correlation between the
experimental factors and output responses. The predicted R2
value of 0.8985 is in reasonable agreement with the adjusted R2
value of 0.949, as shown in Table 5.
Table 4 Response Surface Regression: TS versus Tp,
Vf ANOVA
Table 5 Response Surface Regression: MH versus Tp,
Vf ANOVA
3.3.1.1 The adequacy of the
models with significant terms
Pareto charts of the standardized
effects in Figure 3 (a) and (b) illustrate that the main influence factors on
the responses are Tp and then Vf, where TP and Vf are denoted by the A and B,
respectively. The two-level interaction is significant model term as well.
However, the operating temperature (A) is the most outstanding factor
influencing the UTS and MH. The other factors that exceed the reference line
are insignificant factors.
Figure 4 (a) and (b) show the residual
plots for TS and MH. The bell-shaped and systematic residuals histogram in the
TS graph proves that the ZrO2 volume fraction for the center is
normally distributed and well fit. The normal probability plot of the residuals
is very close to the straight line. Therefore, the errors are minor and
normally distributed. The randomly scattered points reveal the equal
distribution and constant variance. The interaction between temperature and
volume fraction has significant effects on TS and MH responses.
Figure 4 (a) Residual plots for UTS and (b) MH Residual plots |
3.3.2 Developing Empirical Model
The final regression model was
constructed using Minitab 18 to predict TS and MH of the composite as expressed
in equations 8 and 9.
Linear regression
analysis identifies correlations between response and predicted variables. Both
equations indicate that temperature has more effect than ZrO2.
3.3.3 Optimization
The RSM was used to optimize UTS and MH
by analyzing the input factors to acquire the optimal values that result in
maximum UTS and MH. According to RSM optimization results 550 °C and 10.1515
wt% are the optimal parameters yielding maximum TS and MH values of 261.53 MPa
and 132.4 HV, respectively. The Optimized solution is consistent with
experimental results of 262.5 MPa and 135.5 HV.
Table 6 Optimization
Result for UTS and MH
3.4. Confirmation Test and Validation
Three confirmation tests were performed for
empirical result validation. The specimens were prepared based on optimal
parameters settings of 550 °C and 10.15 wt %.
to validate the quadratic regression model. The average error between
the experimental value and the predicted model is less than 2%. The predicted and measured UTS agreed well, thus results
confirm the reproducibility of the experimental data.
Table 7 Results of the Experimental Validation
Figure 5 (a–c) of SEM micrographs shows a
fracture surface of the tensile profiles for sample S1 forged at 450 °C and
reinforced with 5 wt % ZrO2. Sample S1 possessed the lowest YS of
55.89 MPa (Table 3). Surface morphology was visualized utilizing SEM (Hitachi
SU1510). Prominent crack ridge and periphery coarse topography appear in Figure
5b. The low temperature and volume fraction led to poor chip bonding, revealing
long cracks and ridges instead of equiaxed dimples. The partial oxide layer
destruction between chips impeded complete welding and indicated the effect. It
is related to oxidation between layers and chip boundaries, preventing grain growth
due to chip boundaries
Figure 5 (d–f) shows the fracture
surface topography of S13: 550 °C-preheated and 10 wt % ZrO2. The
sample demonstrated the highest UTS of 262.52MPa. The positive influence of
high temperature is proven in the sample fracture mechanism. The crack
initiation zone at 70× magnification is characterized by periphery coarse and
quasi-cleavage, as depicted in Figure 5 (e). Microvoids and dimples indicated a
ductile fracture mode. Numerous small dimples demonstrated the effect of high
temperature and volume fraction on the behavior of fracture surfaces. The
coalescence occurs when reinforced material elongates to initial spaces leading
to a dimpled appearance Figure 5 (f). However, the dimples were not uniformly
formed; some differences in size were apparent.
Figure
6 (a–d) of SEM micrographs depicts a fracture surface of tensile profiles for
S0 (non-reinforced specimen) with 550 °C and 0 wt % ZrO2.
This sample was prepared from pure chips (without reinforcement) to study the
fracture behavior differences between ZrO2-reinforced and
non-reinforced specimens. The top view of the fracture surface is characterized
by the morphology of primary and secondary cracks, as shown in (a). The crack
propagation in Figure 6 (e) started from the weakest points of the chip
boundaries due to the precipitation and the chip's large surface required high
consolidation. The interfacial bonding between Al-chip and ZrO2
reinforced material minimizes the porosity as prominent in SEM images shown in
Figure 6 (f). Microvoids are visible in some regions in Figure 6 (d),
indicating the ductility of recycled material.
Figure 5 SEM micrographs of the tensile profiles for 450
°C, 5 wt % ZrO2 (S1): (a) an overview of the brittle fracture
surface, (b) the quasi-cleavage fracture surface, (c) the observed ridges, and
SEM micrographs of tensile profiles for 550 °C, 10 wt % ZrO2 (S13):
(d) homogeneous distribution of ZrO2 in matrix, (e) the cleavage
facet and crack topology and (f) fine equiaxed dimples
Figure 6
SEM micrographs of the tensile profiles for 550 °C, 0 wt % ZrO2
(S0): (a) an overview of the fracture surface, (b) the cracks on the chip
boundary at 35× and (c) 500×, (d) cleavage-like and dimples, (e) cracks on the
chip boundary and (f) microvoids appearance at 500×
3.6. Analysis of Relative Density
As
shown in Figure, the lowest density of 2.74
g/cm3 was attained at 450 °C, 15 wt % ZrO2, while
the 550 °C, 10 wt % sample recorded the highest density of 2.83 g/cm3.
The density increased by 2.47%, from 2.76 to 2.8281 g/cm3, when the
forging temperature was varied from 450 to 550°C with a fixed 10 wt % ZrO2.
Although the samples were cold-compressed at the same 35 ton pressure, the
higher temperature made a difference in reducing voids, as supported by UTS
results. Additionally, the zirconia's high density of 5.68 g/cm³ contributes to
improving the total density of composite material
The maximum UTS of 262.5 MPa was obtained with
10 wt % ZrO2 + 90% chip at 550°C, showing 23.18% higher UTS than the
100% chip sample. However, UTS began to drop when the volume fraction of ZrO2
exceeded 10 wt %. The highest microhardness of 135.5 HV was attained with 10 wt
% ZrO2 and 550°C. The density increased from 2.76 to 2.83 g/cm3,
by increasing the processing temperature from 450 to 550 °C for the sample with
10 wt % ZrO2. The average grain diameter increased with operating
temperature and decreased with increasing ZrO2 content above 10%.
SEM micrograph revealed a uniform distribution of ZrO2 particles in
the matrix. ANOVA with RSM analysis revealed that TP was the most influential
factor in UTS and MH responses. However, Vf had a considerable effect on
responses as well. The optimization results suggested 550°C and 10.15 wt% as
optimal parameter settings for maximum UTS and MH. The average error between
experimental and predicted optimal results was 1.9%, indicating a high
correlation. The reinforcement material and chip morphology should be
studied further in order to improve composite quality and expand its
application limits.
Communication of this research is made
possible through monetary assistance by Universiti Tun Hussein Onn Malaysia and
the UTHM Publisher's Office via Publication Fund E15216. The authors express
their profound appreciation for the supplementary provisions provided by
Sustainable Manufacturing and Recycling Technology, Advanced Manufacturing and
Materials Center (SMART-AMMC), Universiti Tun Hussein Onn Malaysia.
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