Indian Journal of Materials Science
Volume 2015 (2015), Article ID 756219, 10 pages
http://dx.doi.org/10.1155/2015/756219

Research Article

Effect of MgFeSi Inoculant on Properties of Cast 6061 Al Alloy for Brake Master Piston Application

Olawale Olarewaju Ajibola1,2 and Daniel Toyin Oloruntoba¹

¹Metallurgical and Materials Engineering Department, Federal University of Technology Akure, Akure 340252, Nigeria
²Materials and Metallurgical Engineering Department, Federal University Oye Ekiti, Oye Ekiti 371104, Nigeria

Received 13 May 2015; Revised 2 September 2015; Accepted 15 September 2015

Academic Editor: Kwo Young

Copyright © 2015 Olawale Olarewaju Ajibola and Daniel Toyin Oloruntoba. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

Abstract.

The influence of varying amount of MgFeSi inoculant on properties of cast 6061 Al alloy for brake master piston application has been studied and reported in this paper. Cast samples were produced at three pouring temperatures (700, 750, and 800°C) with MgFeSi varied from 1 to 3%. Wear resistance tests were performed on cast alloy in brake oil. Wear resistance tests results were validated by nondestructive examinations using photomicroscopy, SEM, EDX, and XRD data. The addition of MgFeSi influenced both the mechanical (hardness, strength, and wear resistance) and metallurgical properties (microstructures) of the cast alloy. Al grains were more refined and yielded good strength properties. Inoculating the melt with MgFeSi forms insoluble compound particles and is responsible for grain refinement. The increased amount of MgFeSi from 1 to 3% improved the wear resistance of the cast piston under lubricating condition using brake oil.

1. Introduction

The application and acceptability of sand casting are an important aspect of foundry/casting practices ranging from the numerous cottage and large-scale manufacturing industries [1]. Small and large engineering components (machine parts) are made from different metals and alloys such as steel, cast iron, copper, bronze, brass, and many other known aluminium alloys. The right practice of casting starts with the understanding the control and chemistry of the melt. Casting aluminium alloy entails proper handling of materials: type of furnace, fuel, the melting pot, the selection of fluxing additives, alloying elements, and the moulding sand composition. Superior properties can be achieved in aluminium alloys through systematic control of casting processes.

Literature is scarcely available on the MgFeSi inoculation of Al alloys, but some latest progress on reports of inoculants in alloy and casting similar to MgFeSi in Al alloys. These include inoculation treatment of ductile iron [2], cast iron [3], oxide particles inoculant in Al alloys [4], and pure aluminium inoculation treatment with titanium and boron [5–8]. The current study reports the effect of MgFeSi inoculation as a means of grain refinement and enhancing the mechanical properties (strength, hardness, etc.) of Al alloys.

The mechanical strength, hardness, and the microstructure of the aluminium cast could be improved by controlled melting, pouring temperature, and the solidification processes and proper management of other different controlling factors [9–12]. The pouring temperature for aluminium alloys usually ranges from 720 to 790°C, even though thin-section cast products can be poured at temperatures as high as 845°C as found in the literature [8].

The moulding sand permeability influences the cast product quality. The pouring temperature, solidification, and cooling rate are tailored to control the microstructure of the cast aluminium alloy. This influences the piston making [13, 14] and it also affects the hardness of the cast alloy. This is in agreement with other researchers [10, 15]. The hypereutectic aluminium alloys (390, B390, and 393) are used primarily for wear applications (engine blocks, compressors, pistons, pumps, pulleys, brake systems, etc.). They are also used for thin parts since they have exceptional fluidity [9, 16].

In this work, the Al-Si alloys are produced by sand casting. This technique is identified as a relevant method for the production of many aluminium alloy parts with outstanding metallurgical properties suitable for the desired level of application. In designing a right alloy for the production of cast piston, each of the alloying elements plays a significant role. It has considerable influence on the properties of the cast piston. For purposes of understanding the effects and importance of alloying elements, the alloying elements contained in the as-received piston are classified into three as major, minor, microstructure modifiers or impurities. Conversely, the impurity elements in some alloys might be major elements in others. The major alloying elements typically identified in scrap aluminium alloys are silicon (Si), magnesium (Mg), and copper (Cu). In general, the microstructure modifying elements are titanium (Ti), manganese (Mn), and chromium (Cr). The impurity elements are iron (Fe), chromium (Cr), and zinc (Zn) [9]. The copper in alloy imparts good strength and hardness, making it heat treatable, and possesses enhanced machinability.

The only deliberate and guarded additions of zinc (Zn) to aluminium casting alloys are in the 7XXX series. It happened just as an acceptable impurity element in many secondary (scrap-based) casting alloys. It is quite neutral; it neither adds nor subtracts alloys properties. Zinc is a dense (heavy) element, and it increases the alloys mass density [9]. The behaviour of Al-Si alloy can be explained using Al-Si phase diagram. In the present study, the amount of Si ranged from 0.7 to 1.3 approximate values from the as-received scrap to the cast Al with inoculant as in Figure 1.

Figure 1: The aluminium-silicon phase diagram [17].

The equilibrium phases diagram for the binary Al-Si system is shown in Figure 1. Hypoeutectic alloys are alloys having silicon content less than the eutectic composition. Many common hypoeutectic alloys fall between 5% and 10% silicon. It is conventional that the eutectic reaction occurs with 12.6% silicon at 577°C temperature [17]. A substantial quantity of Si dissolves in solid Al at higher temperatures. The maximum solubility is seen to be 1.6% at the eutectic temperature whereas only an insignificant quantity of Al dissolves in Si. Considering different phase diagrams for the Al-Si system in various literature, there are discrepancies as to the exactness of the eutectic composition and, to a less significant extent, the eutectic temperature. This is because the Al-Si eutectic formation is very responsive to a small change in quantity of impurities, particularly P, Na and other alkaline earth elements.

Eutectic alloys are formed between 10 and 13% Si and consist principally of Al-Si eutectic in the cast structure characterized by the following: a narrow range of freezing points, exceptional fluidity, high castability, and good wear resistance [13]. It is moderately ductile when being not alloyed and heat treatable to high strength property. When containing Cu, Mg, and occasionally Ni, eutectic Al alloys are used extensively for pistons. Cast hypereutectic alloys are obtained between 15 and 20% Si. The cast structure is made of primary Si particles entrapped in Al-Si eutectic matrix. They have good high-temperature strength with remarkable wear resistance but low machinability. They are good for pistons, engine blocks, and compressor components [13, 14]. FeSiMg is widely used in the steelmaking and cast iron production and casting but literature is scarcely available (if any) on the use of FeSiMg in Al alloy casting. Thus, this is newly and briefly examined in the study. The hardness values and the mechanical strength are the only properties that are quantified in the study. Focus is given to the effect of the inoculant variation on the microstructure. Nevertheless, brief explanations were mentioned within the text. The authors had reported the mechanical properties of cast Al alloy in the previous study [13, 14].

2. Materials and Method

2.1. Production of Cast Aluminium Alloy Samples

Aluminium alloy scrap was obtained from the brake master piston. A branded FeSiMg7Re1 with code name 7-1 was obtained from the chemical store. About 2 kg of the scrap was charged into the melting pot, fired, and melted using Taifa model electric furnace. The molten alloy was held for 10 minutes at three pouring temperature ranges between 750 and 800°C under a controlled atmosphere before pouring. Various quantities (1–3%) of MgFeSi inoculant were used to treat molten Al metal. The procedure followed is similar to cast iron [3]. The moulding flasks were preheated before the casting process. The cast-aluminium-alloy samples were obtained at pouring temperatures of 750 ± 10°C. The molten metal was allowed to solidify and cool to obtain eutectic Al-Si structured phase. The cast samples were removed from the sand mould, fettled, brush cleaned, and lightly machined on the lathe to get a rod of 300 mm length and 25 mm diameter. The cast (rod) was later cut to 2 mm thickness by 25 mm diameter for further processing.

3. Experimental Details

The hardness tests of Al alloy samples were determined using Brinell Hardness Tester. The microstructures of samples were examined by using a High-Resolution Metallurgical Microscope with the digital camera (Nikon-Eclipse M600 model). The sections were examined under different magnifications (×10, ×100, ×200, ×400, and ×800).

The chemical composition of the cast samples was characterized by Atomic Absorption Spectroscopy (AAS-Thermo series 2000 model). The X-ray diffraction XRD (Mini-Diffractometer MD-10 model with digital facilities) was used to determine grain sizes and possible phases. In addition, Scanning Electron Microscope with Energy Dispersive X-ray facilities (Jeol JSM-7600F Field Emission SEM/EDX) was used to examine the microstructures at high magnifications.

The study evaluates the surface integrity of cast samples by wear tests with the view to assessing the performance of the cast piston specimens in brake fluid. The wear tests were performed on the as-received (AR) scrap pistons and cast piston samples (with and without varying amount of MgFeSi) using a Wear Jig [13, 18, 19]. The samples are inserted into the Wear Jig and run for wear cycles range of 1225 to 122500 cycles varied at 1225 interval. The wear resistance is determined from wear volume (loss). The maximum volume loss of wear that can occur is described by [20] in Archard’s equation:

where is the volume of substance removed, is the distance slid, and is the cross-sectional area of the groove. Wear resistance is defined as the reciprocal of wear volume (in cm⁻³ or mm⁻³) as in

The results of wear tests were used to interpret microstructural details, XRD, SEM/EDX, and AAS data generated from the research.

4. Results and Discussion

The chemical compositions of the as-received scrap alloy and the cast aluminium alloy samples used in this experiment are presented in Table 1(a).

Table 1: (a) AAS analyses of aluminium alloy samples. (b) Composition of the branded FeSiMg7Re1 powder.

(a)

Samples
Al
Fe
Si
Mg
Cu
Zn
Ti
Mn
Cr

As-received Al scrap
98.665
0.232
0.686
0.403
0.001
0.001
0.001
0.001
0.001

Cast Al (no inoculant)
98.44
0.163
0.327
0.294
0.01
0.001
0.001
0.001
0.001

Cast Al (with inoculant)
97.432
0.331
1.293
0.598
0.202
0.001
0.051
0.051
0.041

(b)

Brand tag
Mg
Re
Si
Ca
Al
Fe

FeSiMg7Re1
6.0–8.0
0.5–1.5
38–44
1.0–1.5
<1.0
44–53.5

Meanwhile the chemical composition of the branded FeSiMg7Re1 powder used for the present work as given by the manufacturer is presented in Table 1(b)

The wear resistances (in oil) of cast aluminium alloy piston with and without MgFeSi additive are compared in Figure 2. It is obvious that the addition of MgFeSi has a positive influence on all the alloys tested. Higher wear resistance performance was obtained from the present work using 3% MgFeSi as compared with the results reported previously by Ajibola et al. [13, 14].

Figure 2: Result of wear resistance tests of as-received (AR) piston scrap and cast piston samples with varying percentage of MgFeSi in oil.

The wear resistance of all the Al alloy materials reduces with the increasing number of the wear cycles. The as-received Al alloy wears at a very close trend of wear rate as the 1% MgFeSi inoculated Al alloy. It is evident from the result (Figure 2) that there is increased wear resistance that results from the increased content of MgFeSi from 1% to 3%.

5. Microstructural Examination Scrap Sample and Cast Samples

The surfaces and microstructures of scrap samples and cast samples studied using higher resolution metallurgical microscope with digital camera and SEM under different magnifications are shown in Figures 3–10(b). The EDX data are integrated into Table 2 for easy comparison. The table describes the composition of the grains of cast Al alloy (with and without inoculant) and the grain boundary (with inoculant).

Table 2: Composition of the grains and the grain boundary (with and without inoculant).

Element (wt%)
C
O
Mg
Fe
Si
Zn
Cu
Al
Mn

Cast Al alloy grains (without inoculant)
7.36
7.73
1.65
1.43
1.31
1.04
1.21
78.27
—

Cast Al alloy grains (with inoculant)
4.15
3.75
2.36
3.51
2.25
1.85
2.86
78.11
1.16

Cast Al alloy grain boundary (with inoculant)
6.55
8.08
2.43
4.27
3.39
1.71
1.34
72.23
—

(a) 1% MgFeSi

(b) 2% MgFeSi

(c) 3% MgFeSi

Figure 3: Surfaces of as cast aluminium alloy with varying percentage of MgFeSi (×10).

(a) 1% MgFeSi

(b) 2% MgFeSi

(c) 3% MgFeSi

Figure 4: Porosity of surfaces under microscopic camera (×100).

(a) 1% MgFeSi

(b) 2% MgFeSi

(c) 3% MgFeSi

Figure 5: (a) Cracks due to hot tearing; ((b)-(c)) topography and roughness of cast surfaces (×1000).

(a)

(b)

(c)

(d)

(e)

(f)

Figure 6: Microstructure of (a) as-received AR scrap Al alloy and cast piston with varying percentage of MgFeSi ((b) 0%, (c) 1%, (d) 2%, (e) 3%, and (f) 3% (iron-rich Al₅FeSi phase)) poured at 750°C (×800).

(a)

(b)

(c)

Figure 7: Microstructure of cast piston ((a), (b), and (c)) with nucleation of larger number of small grains with 3% MgFeSi poured at 750°C (×800, ×400, and ×200).

(a) 1% MgFeSi (700°C)

(b) 1% MgFeSi (750°C)

(c) 1% MgFeSi (800°C)

(d) 2% MgFeSi (700°C)

(e) 2% MgFeSi (750°C)

(f) 2% MgFeSi (800°C)

(g) 3% MgFeSi (700°C)

(h) 3% MgFeSi (750°C)

(i) 3% MgFeSi (800°C)

Figure 8: Effects of varying percentage of MgFeSi and casting temperatures on microstructure of cast piston (×800).

Figure 9: SEM electron image showing the microstructure of cast Al alloy (without inoculant).

(a)

(b)

Figure 10: (a) SEM electron image showing target grain of cast Al alloy (with inoculant). (b) SEM electron image showing target grain boundaries of cast Al alloy (with inoculant).

The images in Figures 3(a)–3(c) show the surface appearances of the as-cast AA6061 Al alloy with varying percentage of MgFeSi observed at ×10 magnification. For the reason of better clarity, Figures 4(a)–4(c) are the enlarged view of the same set of surfaces examined at ×100 magnification. It could be observed that the cast surface appearance seems to improve with the increasing quantity of MgFeSi. The pores in the cast are clearly revealed for each quantity of MgFeSi inoculant added. The 1% MgFeSi cast product appears woolly with the combination of both large and fine pores. The SEM images in Figures 5(a)–5(c) show some other casting defects such as the cracks due to hot tearing and roughness of cast surfaces.

The chemical analysis shows that 98.665% Al, 0.686% Si, 0.403% Mg, 0.001% Cu, 0.001% Zn, 0.001% Ti, 0.001% Mn, 0.001% Cr, and 0.232% Fe are present in the scrap aluminium alloy. The identified trace elements or impurities are inevitably present in primary Al and consequently are found downstream in wrought and foundry alloy products. The reduction in grain size is obtained by the nucleation of the aluminium phase that was achieved through MgFeSi inoculants used to provide the necessary nuclei. In the present study, the addition of MgFeSi initiated nucleation in collaboration with other factors like alloy composition, cooling rate, and the temperature gradient in the melt. With the addition of MgFeSi powder, 97.432% Al, 1.293% Si, 0.598% Mg, 0.202% Cu, 0.001% Zn, 0.051% Ti, 0.051% Mn, 0.041% Cr, and 0.331% Fe were obtained in the cast piston. It is explained that there is increase in the % Fe composition in the cast piston. This may be from both MgFeSi inoculation and/or the Fe pickup from the steel container (melting pot) due to higher solubility of Fe in molten Al [21].

The formation of MgAl₂O₄ and the MgAl₂O₄ particles is got from the addition of 0.49~0.70 wt% Mg to pure Al [4]. But with the addition of 1–3% MgFeSi to the melt, large amount of Mg is dissolved and forms compounds such as MgO·Al₂O₃ and Al₂CuMg (Table 4). The MgFeSi supplies more Mg, Fe, and Si into the Al melt. Among all, silicon (Si) is the most noteworthy single alloying constituent in many of aluminium casting alloys. Silicon is primarily accountable for good castability, with no hot tearing or hot cracking defects as depicted in Figure 5(a).

Silicon plays a vital role as an alloying element manyfold. Figure 5 shows the influence of increasing MgFeSi content on the cast alloy property. In Figure 5(a), the cast alloy exhibited cracks, while microstructure details in Figures 5(b) and 5(c) are of better qualities. The white-marked areas in Figure 5(a) denote the traces of cracks due to hot tearing on the faces of cast Al alloy (without MgFeSi) during solidification, though silicon has limited solid solubility (maximum 1.65%) and can form a eutectic solution with aluminium at a significantly high level to ~12.6% (Figure 1). MgFeSi inoculation imposed more Si dissolution in the system and thus formed eutectic with aluminium to ~2.25–3.39% in (Table 2). Silicon is a very hard phase that contributes significantly to aluminium alloy wear resistance [13, 14, 22]. It joins other elements to enhance the alloy mechanical strength (Table 3) and to make alloys heat treatable [23].

Table 3: Effects of varying percentage of inoculant on mechanical properties of cast Al alloy samples.

Sample
% MgFeSi
BHN
Pnt 1
BHN
Pnt 2
BHN
Pnt 3
BHN
Pnt 4
Average
BHN
Strength
(MPa)
Observation
(porosity, etc.)

Cast-01
0
61.3
60.8
63.2
64.3
62.4
224.83
Cracks, pores

Cast-02
1
63.4
64.4
64.1
63.3
63.8
226.49
More pores

Cast-03
2
64.3
62.6
65.9
65.8
64.6
229.46
Fewer pores

Cast-04
3
61.4
71.2
69.4
60.8
65.7
237.14
Few pores

Table 4: XRD analysis for cast Al sample with 3% MgFeSi.

Peak
Crystal structures
Phases
Diffraction angle (2θ)
Grain size (Å)

0.20
Cubic
Al₂CuMg
18.4317
0.18

0.10
Cubic
Al₁₅(MnFe)₃Si₂
20.1235
0.15

0.15
Tetragonal
MgO·Al₂O₃
27.3567
0.15

0.03
Triclinic
Al₂Si₄O₁₀
29.5332
0.05

0.70
Triclinic
Al₂Si₄O₁₀
36.3582
0.05

2.00
Triclinic
Al₂Si₄O₁₀
36.8058
0.38

0.15
Monoclinic
AlCu
38.0476
0.10

0.60
Monoclinic
SiO₂
39.2411
0.60

0.45
Triclinic
Al₂Si₄O₁₀
43.6492
0.34

0.50
Cubic
Al₅FeSi
47.1035
0.29

0.15
Cubic
Al₅FeSi
49.0033
0.25

0.35
Tetragonal
SiO₄
55.0069
0.14

0.15
Tetragonal
Al₂CuMg
56.3417
0.21

0.15
Tetragonal
CuAl₂
65.2541
0.15

0.15
Cubic
Al₂CuMg
66.7506
0.13

0.55
Hexagonal
SiO₂
71.1864
0.11

Approximate.

The presence of magnesium (Mg) as alloying element strengthens and hardens aluminium castings (Table 3). The presence of Mg phase contained in the alloy was identified and diffracted as Al₂CuMg and MgO·Al₂O₃ in the XRD analysis of the cast sample (Table 4). The combination of Tables 3 and 4 may explain why the cast piston has high wear resistance compared to the as-received scrap piston sample (Figure 2).

In Figure 8(g), for casting at 700°C with 3% MgFeSi, the microstructure revealed the presence of undissolved MgFeSi (black portions) locked up in the matrices of the cast Al alloy (white segments). That was not observed at 750 and 800°C in Figures 8(h) and 8(i). This structure looks similar to a “bull eye” structure obtained previously from the addition of MgFeSi to cast iron by Alasoluyi et al. [3]. Figure 10 presents the microstructure of cast Al alloy with MgFeSi. The examination of the EDX data (Table 2) revealed the effect of the MgFeSi on the microstructure (the grains).

By combining the EDX data (Table 2) and XRD results (Table 3), it can be inferred that copper (Cu) among the alloying elements singularly has the greatest impact on the strength and hardness of cast aluminium alloys. In the present work, Al₂CuMg, AlCu, and CuAl₂ structures are identified and diffracted in the cast sample by XRD analysis. A substantial amount of Cu (1.21~2.86% wt) was revealed in the EDX data for all samples (Table 2). It is known that copper improves the machinability of the alloys by increasing matrix hardness, making it easier to generate small chips of cuttings and smooth machine finishes on the lathe and mill.

Trace quantities of three major microstructure modifying alloying elements (Ti, Mn, and Cr) are detected as inherited from the as-received scrap sample in the AAS data (Table 1). With titanium (Ti) present in the alloy, it forms TiAl₃ and refines primary aluminium grains or nucleates primary aluminium dendrites [24]. Szajnar and Wróbel [8] had established that the rise in size decrease of Al after inoculation with (Ti+B) results from the Ti₃Al and CuTi₂ to heterogeneous nucleation formation. This is because Ti₃Al and CuTi₂ compounds are the foundation for heterogeneous nucleation and powerfully affect size reduction enhancement in aluminium structure. When nucleation is more frequent, a large number of smaller grains (refined grains) is often obtained as seen in Figures 8(a)–8(h).

At temperature as high as 750°C, there are subsequent structural changes occurring when aluminium alloy forms an amalgam with Mn and/or Cr (Table 1). Report shows that Al alloy combined with Mn and/or Cr. That changes the customary platelet structured morphology to the Al₁₅(MnFe)₃Si₂ cubic phase (Figure 6(e)) from the iron-rich Al₅FeSi phase (Figure 6(f)). The obtainable size and amount of the Al₁₅(MnFe)₃Si₂ cubic phase have been reported to be a function of the concentration levels and solidification rate [9, 14].

Iron (Fe) is present in most traditional casting alloys as a very useful impurity. The supersaturated molten alloy can dissolve the relatively unprotected and exposed tool steel while the molten alloy is in close contact. MgFeSi inoculation supplies Fe and Si, which combines with aluminium and other elements to form a mixture of hard, insoluble complex phases and is shown in Figures 6(b)–6(f). The Al₅FeSi phase forms very thin platelets in the form of broom-like structures (Figures 7–10(b)).

In the present study, some of the specimens are cast at varying temperature 750 ± 50°C using moderately high moulding sand permeability [25]. Pouring an aluminium alloy at a temperature above 700°C often gives improved metallurgical properties such as strength, hardness, porosity, and microstructure [9–11, 13]. The option of a pouring temperature at 750 ± 10°C is to moderate the gas content in the molten aluminium alloy and to obtain eutectic structure of cast alloy [25]. If the temperature of molten metal (especially for molten aluminium) is higher, the gas content increases, thus increasing the cast porosity if not properly managed by degassing methods.

The micrographs of the scrap alloy and cast aluminium alloy poured at 750°C are presented in Figures 6(a)–6(f) and 7(a)–7(c). The images in Figures 7(a), 7(b), and 7(c) were observed at ×800, ×400, and ×200 magnifications. The microstructures of the cast Al alloy with 3% MgFeSi appear with nucleation of larger number of small grains. The differences and similarities between the structures and grain sizes of scrap alloy and cast samples are compared in the study. This is with respect to the pouring temperature and MgFeSi inoculation. The as-received scrap alloy has more coarse grains (Figure 6(a)) than the cast samples (Figure 7(c)). Microstructures of as-received scrap alloy and cast samples are examined under higher resolution metallurgical microscope with a digital camera. An optical micrograph of the binary Al-Si alloy is shown in Figures 6(b)–6(d). The dark areas of the Al-Si eutectic and brighter areas of Al are observed with the eutectic Si. This possesses very fine transitional Al-Si eutectic according to the American Foundry Society (AFS) modification rating system [11, 26].

The microstructural details show different phases resulting from the increase in content of Si, Mg, and Cu. Aluminium is lost to dross at high temperatures above 670°C (being understood from the dross theory), with consequent Fe pickup from the melting pot and cleaning tools, thus adding more to Fe content already present in the commercial alloy sourced from the as-received piston.

In the present work, adding MgFeSi inoculant to the molten Al forms different phases with enhanced properties. The aluminium alloy consists of Al₂Si₄O₁₀, Al₁₅(MnFe)₃Si₂, Al₂CuMg, and Al₅FeSi phases in eutectic Al-Si structures. Si combines with Mg to form Mg₂Si, which is soluble in the solid alloy. When combined with copper, it forms the precipitation-hardening phase, Al₂CuMg [21], and some other compounds like AlCu and CuAl₂. Subsequently, giving the cast alloy higher hardness and strength, thus these influenced the higher wear resistance value than the as-received scrap alloy.

Furthermore, the removal of oxide inclusions is one of the main challenges of recycling aluminium alloy scrap. At high temperatures 750 and 920°C, γ-Al₂O₃ platelets and α-Al₂O₃ particles are, respectively, formed in molten commercially pure Al [4]. In the present instance, the oxidation on the surface of Al alloy melts is inevitable at high temperature due to the high affinity between the oxygen and Al when exposed to oxygen containing atmospheres. The various oxides (MgO, Al₂O₃, SiO₂, and Al₂Si₄O₁₀) formed at the surface of the melts are easily entrapped in the castings while stirring, skimming, and pouring [27–30]. The intensive “shearing” (resulting from stirring, skimming, and pouring) of the melts prior to solidification breaks up the oxide films and scattered the strong oxide particles within the melt which in turn improved the heterogeneous nucleation and results in the grain refinement. Consequently, there are increases in the hardness and strength of the Al alloy. The grain sizes are calculated from the combination of Bragg’s law [31] and Scherrer’s equation [32] in

where is the intergranular spacing, is the wavelength, and is the order of reflection of the X-ray.

Additionally, the estimated average grain sizes of the Al alloy are presented as the approximate values (Table 4), determined from Scherrer’s equation in (4).

Whereas 0.9 is the constant shape factor, relates to line amplification at half of the maximum intensity (in radians), and is the Bragg’s angle and is the mean (average) size of the ordered crystals.

The diffraction angle is related to the grain size by

The SEM electron and EDX of the Al grains and grain boundaries of the cast Al alloy with and without MgFeSi inoculant are illustrated in Figures 9-10(b) and Table 2.

Figure 9 presents electron image of the cast Al alloy (without inoculant). The targeted area contains 1.65% Mg, 1.43% Fe, 1.31% Si, 1.04% Zn, 1.21% Cu, and 78.27% Al as revealed in the EDX spectra data (Table 2). In Figure 10, the SEM image of the cast Al alloy (with inoculant) is illustrated. The 600 μm size area contains by weight 2.36% Mg, 3.51% Fe, 2.25% Si, 78.11% Al, 1.85% Zn, 2.86% Cu, and 1.16% Mn as obtained in EDX characterization data (Table 2). Figure 10(b) shows the SEM image of grain boundaries of cast Al alloy (with inoculant). The 600 μm size area contains 72.23% Al, 3.39% Si, 2.43% Mg, 1.34% Cu, 4.27% Fe, and 1.71% Zn as revealed in EDX studies (Table 2). The results obviously show that the alloy is rich in Si and Mg. The amount of Si present in the molten metal falls within the standard acceptable limit and thus is suitable enough to enhance the flowability, castability, phase transformation, refined sizes (Table 4 and Figure 11), mechanical strength (Figure 12), and the microstructures.

Figure 11: The XRD diffractograms of cast aluminium alloy sample with 3% MgFeSi.

Figure 12: Effect of % MgFeSi increase on mechanical strength and hardness of the cast Al alloy.

The differences in the mechanical properties of as-received scrap and cast samples (with and without inoculant) are reflected in the results tests obtained in combining Tables 1–4 and Figures 11-12. The present results give better insight to understanding the performance and the differences in the wear properties of the as-received scrap and cast test samples previously reported by Ajibola et al. [13, 14, 19, 33]. At large, refined grains and higher values of BHN and strength were obtained as the % MgFeSi was increased from 1 to 3%.

6. Conclusions

Aluminium alloy specimen was produced by sand casting. The addition of MgFeSi produced enhanced properties in the aluminium alloy consisting of Al₂Si₄O₁₀, Al₁₅(MnFe)₃Si₂, Al₂CuMg, Al₅FeSi, and phases in eutectic Al-Si structures, thus giving the cast alloy higher hardness value than the as-received scrap alloy.

Nevertheless, the addition of MgFeSi changes in the chemical composition and influenced both the mechanical (hardness, strength, and wear resistance) and metallurgical properties (microstructures) of the cast alloy. The increased amount of MgFeSi from 1 to 3% enhanced the wear resistance of the cast piston in the brake oil. The grains were more refined as better strength. Inoculating the melt with MgFeSi forms insoluble compound particles, thus helping to increase the rate of nucleation.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

Acknowledgments

The authors acknowledge the staff and management of the Premier Wings Engineering Services and Ado-Ekiti for providing the workshop services for the production and preparation of materials used for the study. The SEM/EDX analysis was performed at the Electrochemical & Materials Characterization Research Laboratory of the Tshwane University of Technology, Pretoria, South Africa, and is hereby appreciated by the authors.

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