Open Access

Synthesis and characterisation of hot extruded aluminium-based MMC developed by powder metallurgy route

International Journal of Mechanical and Materials Engineering201712:2

DOI: 10.1186/s40712-016-0068-9

Received: 11 May 2016

Accepted: 12 December 2016

Published: 11 January 2017



Improvement of the mechanical and tribological properties due to extrusion can be attributed to the improved density and excellent bond strength due to high compressive stress.


To avoid the product defects mathematically contoured cosine profiled die was used for the thermomechanical treatment. Improvement of mechanical characterization like density, hardness, compression test and three-point-bend test was inquired. Two body dry sliding wear behaviour of the prepared AMCs before and after extrusion were investigated by using a pin-on-disc wear testing method by varying the variable parameters like load (N), track diameter (mm) and RPM of the counter disc.


The effect of hot extrusion on mechanical and tribological characteristics of aluminium matrix composites (AMCs) developed by powder metallurgy route followed by double axial cold compaction and controlled atmospheric sintering was studied.


Shearing of the fine distributed graphite particles at the tribosurface acts as a solid lubricant and decreases wear rate. At higher loading and sliding velocity condition a mixed type of wear mechanism was observed.


AMCs Extrusion Density Wear P/M


Aluminium metal matrix composites are the most versatile replacement of other alloys in the sector of automotive, aerospace, defence and sports because of its high strength to weight ratio, ease and prevalence of processing techniques, excellent thermal and electrical conductivity and the ability to sustain in uncertain thermal and mechanical loading environment. This emerging area has influenced the researchers to tailor the mechanical, thermal and tribological properties of the composite using different types of reinforcements with various percentages with types of manufacturing process (Yigezu et al. 2013). The endless process of pursuance of mankind needs the material to behave substantially in critical environments.

Over the last few decades, there has been considerable attention to the evolution of Al-based MMCs developed by powder metallurgy (P/M) route of manufacturing. The main advantage of this kind of manufacturing process is the good distribution of reinforcing particles, low processing temperature and the ability to produce near net shape products with intricate designs (Min et al. 2005; Torralba et al. 2003). A number of studies have been conducted to study the effects of reinforcement of very hard metals as well as ceramics in different grades of aluminium series of powder matrix (El-Kady and Fathy 2014; Jabbari Taleghani et al. 2014; Abdollahi et al. 2014). Layers of oxide formation take place in the P/M specimen during sintering, as aluminium is highly prone to oxide formation. During thermo-mechanical treatments, the covered oxide layer breaks due to highly induced shear stress, leading to a strongly bonded microstructure and improved mechanical properties which eliminate the main drawback of AMCs (Schatt et al. 1997). The use of traditional shear-faced die in extrusion causes product defects owing to the existence of higher velocity relative difference at die exit (Zhang et al. 2012a; 2012b). The use of mathematically contoured die (preferably zero, die entry and exit angle) for the MMC extrusion is highly recommendable.

Ravindran et al. (2012; 2013) investigated the effect of graphite addition, applied load, relative velocity and sliding distance on the wear behaviour of aluminium-based P/M composite. Fine graphite reinforcement acts as a solid lubricant and prevents metal to metal contact so it improves wear resistance compromising with hardness and flexural strength or fracture toughness (Baradeswaran and Perumal 2014; Suresha and Sridhara 2010). The addition of zinc with aluminium improves hot extrudability but decreases the high-temperature performances. Considering these factors, the weight percentage of reinforcements kept less in this work. Improved amount of TiC causes a marginal increase in wear rate, whereas applied load and wear rate varies linearly (Gopalakrishnan and Murugan 2012). Anilkumar et al. (2011) investigated the mechanical properties of the fly ash reinforced aluminium alloy. Improvement of mechanical properties can be achieved by adding more amount of reinforcement by compromising with ductility.

The present investigation focuses on both mechanical and tribological properties of extruded AMC synthesised by powder metallurgy route. Two types of metal reinforcements like Zn and Ti in Al + Mg + Gr matrix has been added for the comparative study. The properties of AMCs before and after thermo-mechanical treatment (extrusion) through a mathematically contoured cosine die were inquired.


Sample preparation

Aluminium, magnesium and graphite in weight percentages of 92.33, 4.26 and 0.85, respectively, were blended for the matrix composition. Two reinforcements, Zn and Ti were added in the mixture for preparing two types of sample. The compositional details of two specimens were tabulated in Table 1. The physical characterisation of the powders like size, shape and flowability was studied. Particle size and shape was analysed by SEM images.
Table 1

Detailed composition



Type 1

Al (92.33) + Mg (4.26) + Gr (0.85) + 1.70 Zn

Type 2

Al (92.33) + Mg (4.26) + Gr (0.85) + 1.70 Ti

The mixture was allowed for uniform blending in a centrifugal blender. The weight ratio of stainless steel ball to powder was maintained 10:1. At an RPM of 200 for 10 h, the mixture was allowed for blending. The flow property of the blended powders was checked by measuring apparent density and tap density of the blended compositions.

The powder was subjected to dual axial compression for the preparation of green pellets. During compaction, the powder inside the container remains in floating condition in between both of the punches. The powder was subjected to a pressure of 275 MPa with a very slow rate of rise and with a dwell period of 10 min. Green density of the prepared 10-mm-diameter pellets was measured. Green pellets were subjected to sintering in a controlled atmospheric tubular furnace in an argon atmosphere. The ramp rate of 5 °C/min was set for all the temperature rises. Dwell period of 20 min at 110 °C to remove water vapour, 30 min at 450 °C to remove lubricant (zinc stearate) and 90 min at 590 °C to form the metallic bond was set for the process.

Secondary processing

The 10-mm-diameter pellet prepared by cold compaction followed by sintering was subjected to thermo-mechanical treatment (hot extrusion) as a secondary processing. The experiment was conducted for 50% reduction of the cross-sectional area of the pellet at an operating temperature of 400–450 °C with a ram rate of 3 mm/min. Extrusion through shear-faced die causes severe surface defects like surface crack and tearing in the extruded product due to velocity relative difference at the die exit. The defects are more prone in the case of extrusion of MMCs synthesised by powder metallurgy route (Prasad et al. 2001). Hence, a specially designed mathematically contoured cosine die from round to square bar extrusion was used for extrusion to avoid severe velocity relative difference. The coordinates of developed profile in one quadrant and the 2D drafting of the extrusion tooling setup are shown in Fig. 1.
Fig. 1

a Profile coordinates of the cosine die profile in one quadrant. b 2D drafting of the tooling setup

Mechanical and tribological characteristics

Theoretical density, tap density, green density, sintered density and extruded density were studied by following the standard procedures. Theoretical density was measured by following the relation mentioned in Eq. 1.
$$ {\rho}_{\mathrm{Theoretical}}={\displaystyle \sum \left({\rho}_{\mathrm{i}}\times {m}_{\mathrm{i}}\right)} $$

ρ i is the density of individual element and m i is the mass fraction of the individual element.

The density of the solid-sintered as well as extruded pellets were measured by following Archimedes’ principle. The relation for calculating the density is presented in Eq. 2.
$$ {\rho}_{\mathrm{sample}}=\frac{W_{\mathrm{A}}\times {\rho}_{\mathrm{fluid}}}{W_{\mathrm{A}}-{W}_{\mathrm{fluid}}} $$

where W A is the mass of the sample taken at atmospheric air, W fluid is the mass of the considered fluid and ρ fluid is the density of the considered fluid.

Vickers micro-hardness of the sintered MMC composite was determined by dividing the applied load to the impressed area. 50 g of load were applied through a diamond pyramid having the face angle of 136° for a dwell period of 15 s to avoid spring back effects.

Three-point bend test has been performed to check the transverse rupture strength (TRS) of the sintered solid cylindrical specimen. The test was executed in UTM (universal testing machine, Instron -5979). A span of 30 mm with a compression rate of 2 mm/min at atmospheric temperature was maintained at the time of operation.

Wear testing

Dry sliding wear characteristics of the prepared aluminium MMC was studied by pin-on-disc wear testing apparatus. The pins with dimension 10 × 25 mm were prepared with flat contact surface with smooth corners and kept stationary in the sample holder perpendicular to the counter disc. The rotating EN-31 disc of 60 HRC and average surface roughness value of 2 μm (Ra) was acted as the counter body. The counter disc and pin surface were cleaned with acetone before the experimentation. A normal load was applied on the MMC pellet through the specimen holder by a lever attachment. The line diagram of wear testing mechanism is shown in Fig. 2. The variable parameters like track diameter, normal load and RPM of the disc are well facilitated by the machine set-up, and all are needed to be fixed manually anterior to experimentation. The variable parameters chosen for the wear analysis are tabulated in Table 2. Ten minutes of test duration was adopted for each experiment. With an accuracy of 0.1 mg, the MMC pin (specimen) was weighed before and after the wear operation for determining the wear loss.
Fig. 2

Schematic layout of pin-on-disc wear testing apparatus

Table 2

Variable parameters selected for experimentation

Variable parameters

Level 1

Level 2

Level 3

Wear track dia (D), (mm)




Normal load (L), (N)




RPM of counter disc (N)




Results and discussion

Physical characteristics

Flowability of the powder is directly influenced by physical properties as well as environmental conditions of the powders. The mechanical and tribological properties of the final product are directly related to flowability. Hence, there is a great importance for the study of physical characterisation such as size, shape and densities of the powders. Among the three most popular techniques used for powder size determination like microscopy, laser diffraction and sieve analysis, microscopy and image analysis were performed for determining the size and shape of the powders. The SEM images of all the powders are shown in Fig. 3.
Fig. 3

SEM image of a aluminium, b magnesium, c graphite, d zinc and e titanium powder

Image analysis software package is employed for the analysis of particle size and shape of the powders. The detailed report is presented in Table 3.
Table 3

Physical characteristics of powders



Average size (μm)

Particle shape

Purity/assay (%)


Loba Chemie


Spherical and sub-rounded








Rounded and flakey




Spherical and sub-rounded




Very angular and irregular


Density analysis

Apparent density/bulk density and tap density were recorded from direct measurement. It is depicted from the graph shown in Fig. 4 that 30–35% improvement of density caused by tapping the blended powder. The green density of the pellet primarily depends on the compaction pressure. It was found a good consolidation of metallic particles even in green specimens at 275 MPa. The density was calculated by dividing the measured volume (with the accuracy of ±2%) with the measured mass (with the accuracy of 0.001 g). The non-dimensional densification parameters were calculated by the following relation illustrated in Eq. 3 (Padmavathi et al. 2011).
Fig. 4

Density plot

$$ \mathrm{Densification}\ \mathrm{parameter} = \frac{\left(\mathrm{sintered}\ \mathrm{density}-\mathrm{green}\ \mathrm{density}\right)}{\left(\mathrm{theoretical}\ \mathrm{density}-\mathrm{green}\ \mathrm{density}\right)} $$
Positive densification parameters indicates shrinkage and negative for growth or swelling. All the samples are showing swelling behaviour at the time of sintering. The percentage improvement in densification by thermo-mechanical treatment (extrusion) is calculated by the following relation illustrated in Eq. 4.
$$ \mathrm{Percentage}\ \mathrm{improvement}\ \mathrm{in}\ \mathrm{densification} = \frac{\mathrm{extruded}\ \mathrm{density}\ \hbox{--}\ \mathrm{sintered}\ \mathrm{density}}{\mathrm{sintered}\ \mathrm{density}} $$
There is an increase of 15–20% of density after extrusion with 50% reduction evident in Fig. 4. The calculated values of densification factor, improvement of density and porosities are presented in Table 4. The density of sample type 1 is higher because of higher zinc density.
Table 4

Porosity analysis


Sample 1

Sample 2

Densification factor



Percentage improvement in densification (after extrusion)



Porosity before extrusion (%)



Porosity after extrusion (%)



Compression test of sintered specimen

Compression test of all the two types of pellets was conducted by UTM (Instron-setec series) with the ram rate of 3 mm/min at room temperature. From the output results stress versus strain, curve is plotted in Fig. 5a, b. The average ultimate stress of the two samples is 409, 381 MPa for samples 1 and 2, respectively. The strength of sample type 1 is on the higher side which can be attributed to the excellent bond strength due to liquid phase sintering.
Fig. 5

Stress versus strain for a sample 1 and b sample 2


The average micro-hardness was calculated from the ten readings taken for both sintered and extruded products. Figure 6a shows there exists 35–40% of improvement of hardness in the material after extrusion prepared by the above procedure. It can also be attributed to the higher dislocation density around the reinforcement particles due to the difference of mechanical property and thermal mismatch (Ozdemir and Toparli 2003; Ramesh et al. 2011). The mismatch of the properties between the matrix and reinforcements causes the storage of large internal and thermal stress and engenders improved mechanical properties.
Fig. 6

a Micro-hardness and b transverse rupture strength

3-point bend test

The TRS in MPa found of the specimens was estimated for sintered as well as extruded specimen by following the relations mentioned in Eqs. 5 and 6, respectively.
$$ \mathrm{T}\mathrm{R}\mathrm{S} = 8 Pl/\varPi {D}^3 $$
$$ \mathrm{T}\mathrm{R}\mathrm{S} = 3 Pl/2{d}^3 $$

where P = the maximum load (N)

l = length of the sample (mm)

D = diameter of the sintered specimen (mm)

d = depth = width of the extruded square specimen (mm)

The average TRS for all sintered and extruded sample is presented in Fig. 6b. For the case of sample type 1, presence of zinc having a melting point of 420 °C caused liquid phase sintering at a temperature of 600 °C. In the case of Ti-reinforced sample, there exists a high-stress concentration at the boundary zone of the reinforcements and causes the initiation of fracture so comparatively lesser than TRS.

Microstructural analysis

Figure 7 depicts the scanning electron micrographs of the two types of specimens after the thermo-mechanical treatment at different magnifications. A very little amount of porosity still remains in the material after extrusion which is evident from the figure below. After extrusion operation, the improved density and decreased volume of porosity is illustrated in Fig. 4. The distribution of reinforced particles in the extruded product is uniform and it also shows the good dispersion of reinforcements in matrix elements. There exists a very fine distribution of graphite and other reinforcements like Mg, Ti and Zn. There is no observation of rupture of the reinforcing particle (Ti) in sample type 2 due to the compressive pressure exhibited by extrusion. Also, there is a good bond that exists in between Ti and the matrix element due to its very angular or irregular shape.
Fig. 7

Microstructural analysis of extruded specimen

Wear test

Considering the aforementioned three variables with three levels, an orthogonal array (Table 5) has been designed for experimentation of extruded and sintered samples. The variation of wear rates of sintered, as well as extruded specimen for two types of composites, are presented in Figs. 8 and 9. Mass loss of the pin was estimated from the recorded mass of the sample before and after wear test. The mass loss the test is defined as (Soltani et al. 2014):
Table 5

L9 orthogonal array followed for wear analysis


Load (N)

Track dia (mm)

RPM of counter disc





































Fig. 8

Wear rate for each run for sample type 1

Fig. 9

Wear rate for each run for sample type 2

$$ \varDelta w=\left({w}_{\mathrm{a}}-{w}_{\mathrm{b}}\right) $$

where w a and w b are the mass of the sample before and after the test, respectively.

The volume loss of the AMCs is estimated as the following relation:
$$ \mathrm{Volume}\ \mathrm{loss}\ \left({\mathrm{mm}}^3\right) = \mathrm{Mass}\ \mathrm{loss}\ \left(\mathrm{g}\right)\ /\ \mathrm{Density}\ \left(\mathrm{g}/{\mathrm{mm}}^3\right) $$
The volumetric wear rate Wr (mm3/Km) was estimated by following the relation
$$ {\mathrm{W}}_{\mathrm{r}} = \mathrm{Volume}\ \mathrm{loss}\ \left({\mathrm{mm}}^3\right)\ /\ \mathrm{Sliding}\ \mathrm{distance}\ \left(\mathrm{K}\mathrm{m}\right) $$

Several researchers have reported the direct proportionality relation of hardness with wear resistance. The bond strength between the matrix and reinforcement material improves after extrusion which improves wear resistance, and it also avoids three-body abrasive wear (Ramesh et al. 1992).

Wear microscopy

SEM photomicrographs of the AMCs and extruded specimen for run-2 and 7 are shown in Fig. 10. It is observed there is lesser extent of grooving for extruded specimen than the AMCs. The grooves of the unextruded AMCs are coarse and heavy plastic deformation occuring at the groove linings. Also, granular and flake-like debris are observed around the grooves.
Fig. 10

SEM micrographs of worn surfaces

At higher loading conditions of 40 and 60 N with higher RPM of 600 grooving and scratching plays a predominant role over abrasion. The images showing a large amount of white particles present at the tribosurface which can be attributed to the oxidation of the surface due to frictional heating as the aluminium surface is oxide-prone.

At very high loading and high-velocity condition delamination and combination of abrasion, delamination and adhesion mechanism of wear came into the picture. Due to frequent repetitive sliding behaviour, subsurface crack has been induced due to the fatigue failure of the pin. These subsurface cracks grow with increasing travel distance, and eventually, shear deformation occurs to the surface. Moreover, at the adverse conditions, melting, thermal softening and adhesion take the predominant role to cause plastic deformation. In the case of AMCs, the mechanism of wear is less severe than the base metal alloys. Metal/graphite composite forms a lubricating layer on the tribosurface due to the shearing of graphite particles which prevents the metal to metal contact, causing the reduction of friction and wear.


The effect of extrusion on the improvement of the mechanical and tribological properties of the AMCs was investigated. The results of this investigations are summerised as follows:
  1. (a)

    Mechanical properties of both types of AMCs are improved due to the improved bond strength after extruding it through mathematically contoured cosine profiled die.

  2. (b)

    It was found very less amount of surface defects (few cracks at the corner zone) in the extruded product and supports improvement of flexural strength and tribological properties. Wear rate of the extruded specimen is lesser compared to that of the sintered specimen for each run.

  3. (c)

    The addition of zinc causes liquid phase sintering because of its low melting temperature that leads higher bond strength and density and gives a comparative better performance for the composition. The addition of more amount of fine titanium may improve the properties manifold by compromising with thermal conductivity.

  4. (d)

    Shearing of the well-distributed graphite particles at the tribosurface acts as a lubricant. So, the addition of graphite particle improves the wear resistance by compromising the little amount of hardness.

  5. (e)

    At higher loading and sliding velocity condition, a mixed type of wear mechanism (oxidative, delamination, adhesive and abrasion) takes place. But oxidative and delamination are the predominating wear mechanism found on the surface.



Authors’ contributions

All authors read and approved the final manuscript.

Competing interests

The authors declare that they have no competing interests.

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Authors’ Affiliations

Department of Mechanical Engineering, National Institute of Technology


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© The Author(s). 2017