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05.05.2016 | Ausgabe 6/2016 Open Access

# Properties of Light MMCs Modified with Cordierite Synthesized from Fly Ash

Zeitschrift:
Journal of Materials Engineering and Performance > Ausgabe 6/2016
Autoren:
Piotr Długosz, Angelika Rączka, Adrian Kopeć, Rudolf Krzyżak, Paweł Darłak, Marek Hebda

## Introduction

Composites are a wide group of materials with valuable physical and chemical properties, and present in many fields of industry and science. The design scope for composites is usually focused on several criteria, such as capacity to significantly improve mechanical properties, or capacity to extend the application range, e.g., high-temperature applications, increased vibration dampening performance, increased abrasion resistance, and many more. Whether the designed criteria are met or not is largely conditioned by numerous factors, including composite ingredients’ properties, sizes, shapes, alignment, volume ratio, and matrix reinforcement distribution (Ref 1). Light alloys, e.g., magnesium or aluminum alloys, have become increasingly popular as matrices for MMCs. A specific characteristic attributed to light alloys (aside from their relatively low density) is its favorable strength (R m) to density ratio (or elastic modulus (E) to density ratio). The materials can carry similar static and dynamic loads as iron alloys, albeit having a much lower weight (Ref 2). The development of lightweight structural materials is among the greatest challenges due to, e.g., economic and environmental concerns. Light metal matrix composites allow for significant energy efficiency. Moreover, the materials of this kind contribute to minimum consumption of strategic natural resources (Ref 3). Light metal matrix composites allow for cost effectiveness in operation of transport vehicles, e.g., by reducing fuel consumption while increasing mobility. The promise of these benefits have actually triggered an increased interest in composite materials in most applications such as the automotive, aerospace, and marine industries, just to name a few (Ref 1, 4-10).
A novel approach to the design of metal matrix composites is the application of a reinforcement material derived by synthesis of cordierite (Mg2Al4Si5O18) from fly ash. This synthesis has been performed according to procedure described in (Ref 11). The production of cordierite ceramics from fly ash is inexpensive, while building the ceramic fitting that will act as a pre-mold for saturation of the matrix with the liquid matrix requires no special equipment, foaming agents, binders or hot processing. Cordierite is a natural mineral commercially available in powders, granulates or finished molded pieces. The relatively high purchase pricing substantiates the profitability of synthetic cordierite from fly ash. The cordierite manufacturing process is environmentally friendly, and the resulting fittings see universal use. The manufacturing process is simple and cordierite processing can be quickly adapted for mass production demands without any investment in additional ceramic synthesis machinery (Ref 11). Currently, many methods of fly ash management exist (Ref 12-14). Use of cordierite ceramics synthesized from fly ash in light MMC casting is aligned with the schedule for reduction of the environmental impact of conventional power engineering (e.g. by liquidation of landfills and dumps disposal) and, given the increasing consumption of hard coal, has been becoming increasingly important. Light alloy matrix composites reinforced with cordierite particles are innovative materials that combine high strength with low weight, which may be a key factor to numerous applications of the composite in various industries. Furthermore, production of such materials allows for environmental protection and waste management opportunities.
This paper shows the experimental results from an analysis of the manufacturability of light metal matrix alloys (from AM60 and AK7 alloys) with cheap and easily available reinforcement (cordierite ceramics) synthesized from fly ash. The paper presents the x-ray diffraction (XRD) analysis, the changes in their microstructure as well as the strength properties of the produced materials. Phenomena related to the wettability of AK7 alloy which determine the MMC manufacturability are also discussed.

## Material and Methods

Commonly used casting alloys, the AK7 aluminum alloy and the AM60 magnesium alloys were selected as the metal matrix for the composites. The chemical composition of the alloys is shown in Table 1. The reinforcing material was cordierite ceramics (Mg2Al4Si5O18) manufactured by synthesis of fly ash. The chemical composition is shown in Table 2. Cordierite ceramics was introduced into the matrix at 2 and 4 wt.% as a powder produced by grinding in a high-power ball mill at 1800 rpm for 2 h. The MMCs were manufactured at (ca. 50 °C) above the matrix melting point in the vortex process. The samples were squeeze cast into a dia. 200-mm cylindrical mold at the press force of 160 tons. The reference material selected for the experiments were MMC samples without cordierite, i.e. made of the base alloys (see Table 1) with the identical process.
Table 1
Chemical compositions of the AK7 aluminum alloy and the AM60 magnesium alloy as the metal matrix for the experimentally manufactured composites
Designation
Chemical composition ,wt.%
Si
Cu
Mg
Mn
Fe
Ti
Zn
Al
AK7
7.0
Max 0.05
0.35
Max 0.1
Max 0.19
0.16
Max 0.07
Balance
AM60
Max 0.5
Max 0.35
Balance
0.13-0.6
0.22
5.5-6.5
Table 2
Chemical compositions of the cordierite ceramics as the reinforcement for the experimentally manufactured MMC
Designation
Chemical composition ,wt.%
SiO2
Al2O3
FeO3
MgO
CaO
Na2O
H2O
Cordierite ceramics
45-51
32-35
2-12
3-35
Max 3
Max 3
Max 3
The microsections were visually examined under a Nikon Eclipse ME600 microscope. The chemical composition was analyzed using Jeol 6510LV SEM with an XRF 500 Energy Dispersive x-ray spectroscopy (EDS) module. The phase identification was performed by an x-ray diffraction apparatus PANalytical Empyrean (anode: Cu (copper); counting time 200 s; step of measurement: 0.026°). The static tensile and compressive strength tests were carried out on an MTS Criterion 43 strength-testing machine. The tensile strength test followed the protocol of PN-EN ISO 6892-1:2010 on dumbbell samples with the tension rate of 0.5 mm/min. The compressive strength was tested on cylindrical samples of 5 mm in diameter and 10 mm in height. The traverse feed was 0.5 mm/min. Wettability was examined by the flat drop test with contact heating (Ref 15). The materials were cleaned in an ultrasound washer isopropanol bath prior to the measurements. Next, a drop of the AK7 alloy was laid flat on a cordierite sample and heated at a rate of 10 °C/min to 900 °C, held there for 30 min, and then cooled at 10 °C/min. The measurements were carried out in vacuum. The test subject was recorded in a digital camera during the experiment (with a framerate of 1 fps until the melt-through, followed by 10 pfs until frozen), and the videos served to assess the contact angle (θ). The produced images were digitally processed in the ASTRA software package, developed by CNR-Instituto per I’Energetici e le Interfasi - U.T. di Genova, Italy, to calculate the contact angle.

## Results and Discussion

Figures 1 and 2 show the microsections of the AM60 base alloy and the MMC with 4 wt.% of cordierite ceramics, respectively. The AM60 base alloy seemed to feature two phases (i) the matrix, and (ii) relatively numerous precipitates (indicated as phase 1 in the Fig. 1 and 2), characterized by oblong and/or irregular forms. The distribution of precipitates is very regular, with local joints established between them. It is most likely that the precipitates are crystallized in the areas between the grain boundaries. The MMC structures, both with 2 and 4 wt.% of cordierite ceramics, reveal one additional phase (indicated as phase 2 in the Fig. 2). It is manifest as very fine (needle-like) precipitates that cross one another at the right angle very often. The quantity of the phase increases in direct proportion with the amount of the reinforcement (cordierite ceramics) introduced to the MMC.
However, these variations are not witnessed in the AK7 MMC (Fig. 3). The microstructures of the examined samples were always approximate to the base alloy, irrespective of the amount of reinforcement. Two distinct phases were found therein: (i) the matrix and (ii) a large number of uniformly distributed lamellar/needle precipitates. The lack of microstructural modification may be indicative of failure in their manufacture.
The AM60 MMC as well as AK7 MMC, each with the addition of 4 wt.% of cordierite, were subjected to an XRD analysis to explicitly identify the chemical composition of its phases (Fig. 4 and 5, respectively). The main phase in AM60 alloy was Mg0.976Al0.024 phase (indicated in Fig. 1 and 2 as a matrix). Moreover, the discontinuous precipitation along the grain boundaries, described as phase 1 in Fig. 1 and 2, was Al12Mg17 phase. According to XRD patterns (Fig. 4), Mg2Si phase was only found in the alloys with cordierite ceramics’ addition. This phase was indicated as phase 2 in the Fig. 2. With the increasing cordierite ceramics’ additions, the content of Mg2Si phase increases gradually. Furthermore, XRD spectra show some remnants of the ceramics as MgO phase, while the AK7 MMC mainly contains Al matrix and Al3.21Si0.47 phase (lamellar precipitates) in matrix (Fig. 5).
EDS microanalysis of representative randomly selected areas of the AM60 MMC alloy with 4 wt.% of cordierite ceramics is shown in Fig. 6. The results of the analysis of the specific microstructural areas are listed in Table 3. Figure 7 shows the variations in aluminum- and silicon-content levels in the chemical compositional microanalysis in the area marked with the red line in Fig. 6. Based on the quantitative EDS analysis, it was found where each intersection of the scan lines in Mg2Si-phase measurements caused strong peaks of the silicon-level readings (Fig. 7). The aluminum readings would increase only when Al12Mg17 phase analysis began (Fig. 6 and 7). The results explicitly confirm that an MMC was manufactured, since the silicon detected in the samples (and in the discovered amounts) could only originate from the reinforcing phase, namely cordierite ceramics. Bearing in mind the low amount of silicon in the AM60 alloy, one can suppose that the Si diffuses from the ceramics. Recalling the discussion on the same elements (Mg, Al, Si) in the ceramics and in the alloy, one can suppose the dissemination (and solution) of the elements by the alloy.
Table 3
Chemical compositional microanalysis results for individual phases (shown in Fig. 2) of the AM60 MMC with 4 wt.% of cordierite ceramics
Element, wt.%
Measurement area
Matrix
Phase 1
Phase 2
Mg
100
71.62 ± 6.72
91.20 ± 7.47
Al
28.38 ± 2.55
4.20 ± 1.01
Si
4.60 ± 1.15
The interfacial reaction between the reinforcing phases and the alloy could be conceivable:
$$4{\text{Mg}} + 2{\text{SiO}}_{2} = {\text{ Mg}}_{ 2} {\text{Si }} + \, 2{\text{MgO}}$$
or
$$2{\text{Mg }} + {\text{SiO}}_{2} = {\text{ Si }} + 2{\text{MgO}}$$
The addition of silica and the dissolution of the elements seem to be of paramount importance for investigated composites.
The AK7 MMCs with cordierite were also subjected to the chemical compositional microanalysis (Table 4). Its results reveal that the alloy matrix is made of aluminum, whereas the needle-like precipitates shown in Fig. 3 are a mixture of aluminum and silicon (possibly with low levels of magnesium). In general, composition of the MMC can be approximated to the Al-Mg2Si-Si eutectic. Note that the AK7 base alloy contains ca. 7% of silicon; hence, the measurements disallow any conclusion whether cordierite was introduced or not.
Table 4
Chemical compositional microanalysis results for individual phases (shown in Fig. 3) of the AK7 MMC with 4 wt.% of cordierite ceramics
Element, wt.%
Measurement area
Matrix
Precipitates
Al
100
74.63 ± 6.22
Si
16.49 ± 2.14
Mg
8.88 ± 2.41
Figures 8 and 9 as well as Table 5 show the strength properties of all the tested materials. The results demonstrate that a 2 wt.% addition of cordierite ceramics to AM60 alloy resulted in a nearly twofold increase in tensile strength (relative to the unmodified alloy). Moreover, the elongation of the MMCs grew by three times. The 4 wt.% addition of the reinforcement resulted in worse MMC performance (which were approximate to or sometimes worse than in the AM60 alloy).
Table 5
Strength properties of the experimentally manufactured materials from the static tension test
Material
R m, MPa
R 0.2, MPa
E, GPa
A, %
AM60
97 ± 2.5
54 ± 7.5
27 ± 7.5
2.2 ± 0.1
AM60 ± 2 wt.% of cordierite ceramics
181 ± 25.5
64 ± 8.5
37 ± 4.5
7.3 ± 1.4
AM60 ± 4 wt.% of cordierite ceramics
93 ± 1.5
79 ± 1.5
38 ± 1.5
0.7 ± 0.1
AK7
174.4 ± 0.6
77.6 ± 15.3
47.0 ± 1.7
5.3 ± 0.9
AK7 ± 2 wt.% of cordierite ceramics
142.3 ± 8.8
89.9 ± 15.7
41.2 ± 8.8
1.8 ± 0.6
AK7 ± 4 wt.% of cordierite ceramics
160.7 ± 25.9
85.5 ± 8.6
46.3 ± 2.2
4.0 ± 3.9
The strength properties of the aluminum MMCs are nearly identical to (or sometimes much worse than) the results for the AK7 alloy. Yet again the results confirm that cordierite addition as a reinforcement failed in the aluminum alloy.
The described strength relationships are fully represented in Fig. 10 and 11 that shows the fractographs of the tensile tested sample fractures of the AM60 alloy and the AM60 MMCs with 2 wt.% of cordierite, respectively. All the fractures are quasi-cleavage type in nature. There are facets of quasi-cleavage observed during plastic deformation, resulting in the characteristic cleavage ridges. Increased shares in plastic deformation (in the MMCs with 2 wt.% of cordierite) are evident, e.g., by the pronounced waviness of the fracture, the increased highlight of the cleavage ridge edges, or the larger number of pits that are typical of ductile cracking.
The AM60 MMCs were also subjected to compressive strength testing. The results are shown in Table 6. Again, the highest strength properties were found in the MMC with 2 wt.% of cordierite. Moreover, all the tested samples suffered slip failure by shearing. The extreme tangential stress was at 45° relative to the sample axis.
Table 6
The results of compressive strength testing
Material
R m, MPa
A, %
AM60
371 ± 3.5
26.86 ± 0.82
AM60 ± 2% of cordierite ceramics
393 ± 5.5
26.09 ± 1.16
AM60 ± 4% of cordierite ceramics
339 ± 19.0
20.24 ± 1.97
The produced test results show that the density of input materials of MMCs is not a key factor to guarantee homogeneous introduction of reinforcement to the alloy matrix. Despite the approximate densities of AK7 (ca. 2.7 g/cm3) and cordierite ceramics (ca. 2.6 g/cm3), the attempt to bind the materials had failed. Even with the large difference between the densities of AM60 (ca. 1.8 g/cm3) and cordierite, the MMC was produced without any problems. The results show that densities of the MMCs with addition of cordierite ceramics have not changed significantly relative to the base alloys.
The most probable key effect that guarantees the feasibility of reinforcing the metal matrix is wettability (or the lack thereof) of the reinforcement surface. Wettability analyses were conducted on the AK7-cordierite system to verify this assumption. The measured mean value (of six measurements) of the contact angle (θ) was 149.4° ± 3.1°. The results explicitly prove zero wettability of the AK7-cordierite system.

## Conclusions

The experiments and tests have proven an innovative light metal matrix composite was produced, which has a great potential for various applications. It has also been proven that the AM60 magnesium alloy can be modified by homogeneous introduction of cordierite as its reinforcement. The bonding of the reinforcing phase with the magnesium alloy has been demonstrated to be good. With the proper amounts of reinforcement, the MMCs exhibit better properties than AM60. The highest increment in strength properties (for tension and compression) was observed in samples with 2 wt.% of cordierite. Higher ratios of reinforcement in the magnesium alloy reduce the strength properties.
The attempt to manufacture an AK7 aluminum-based MMC with cordierite has failed. The root cause of the outcome is poor wettability between the aluminum alloy and cordierite.
Moreover, the production of cordierite from fly ash, followed by its application as a reinforcing phase in light alloys, opens new opportunities for fly ash management, which is extremely important due to environmental and cost-effectiveness concerns.

## Acknowledgments

This research was supported by the Project POIG No. 01.01.02-00-015/09
Open AccessThis article is distributed under the terms of the Creative Commons Attribution 4.0 International License (http://​creativecommons.​org/​licenses/​by/​4.​0/​), which permits unrestricted use, distribution, and reproduction in any medium, provided you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons license, and indicate if changes were made.

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