The Scientific World Journal

Volume 2014 (2014), Article ID 106129, 10 pages

http://dx.doi.org/10.1155/2014/106129

Research Article

Effect of Layer Thickness in Selective Laser Melting on Microstructure of Al/5 wt.%Fe₂O₃ Powder Consolidated Parts

Sasan Dadbakhsh1,2 and Liang Hao¹

¹College of Engineering, Mathematics and Physical Sciences, University of Exeter, Exeter EX4 4QF, UK

²Department of Mechanical Engineering, KU Leuven, Celestijnenlaan 300B, P.O. Box 2420, 3001 Leuven, Belgium

Received 29 August 2013; Accepted 1 October 2013; Published 2 January 2014

Academic Editors: V. Calderón, X. Jia, W. Li, and A. Sánchez-Herencia

Copyright © 2014 Sasan Dadbakhsh and Liang Hao. 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.

In situ reaction was activated in the powder mixture of Al/5 wt.%Fe₂O₃ by using selective laser melting (SLM) to directly fabricate aluminium metal matrix composite parts. The microstructural characteristics of these in situ consolidated parts through SLM were investigated under the influence of thick powder bed, 75 μm layer thickness, and 50 μm layer thickness in various laser powers and scanning speeds. It was found that the layer thickness has a strong influence on microstructural outcome, mainly attributed to its impact on oxygen content of the matrix. Various microstructural features (such as granular, coralline-like, and particulate appearance) were observed depending on the layer thickness, laser power, and scanning speed. This was associated with various material combinations such as pure Al, Al-Fe intermetallics, and Al(-Fe) oxide phases formed after in situ reaction and laser rapid solidification. Uniformly distributed very fine particles could be consolidated in net-shape Al composite parts by using lower layer thickness, higher laser power, and lower scanning speed. The findings contribute to the new development of advanced net-shape manufacture of Al composites by combining SLM and in situ reaction process.

1. Introduction

Laser beam provides a flexible and intense energy source for materials processing [1]. Over the last decade, it is adopted for emerging metallic additive manufacturing applications, in particular selective laser melting (SLM) process which directly produces near net-shape or net-shape parts from metallic powders. The SLM process melts and rapidly solidifies a series of layers on top of each other from powder materials to form complex three-dimensional parts [2–4]. SLM has been mostly used to process metals. For example, Louvis et al. [5] have reported the SLM behaviour of Al alloys or Buchbinder et al. [6] have succeeded to manufacture dense Al alloy parts using a very high power SLM machine. However, as a powder based process, it also provides great opportunity to consolidate second or multiple material particles with metal powders to form novel metal matrix composites (MMCs).

There is a growing research to develop MMCs via SLM process [7]. In particular, SLM is being developed to produce in situ composites from powder mixtures in which constituents react together at elevated temperature. In other words, SLM ignites a chemical reaction in the powder mixture besides the melting of metallic powders. The in situ interaction is considered to provide benefits in terms of fine and uniform distribution of compounds, inherent interface between reinforcement and matrix, and exothermic energy to facilitate melting and densification. These benefits have been reported in some pioneering research work on SLM of in situ MMCs. For instance, Dadbakhsh and Hao [8] have studied the SLM of Al/Fe₂O₃ powder mixture for the direct fabrication of in situ Al MMCs. The SLM process was found to be capable of activating an exothermic reaction in the powder mixture for the improved material melting and the formation of homogenously distributed fine alumina and Al-Fe(-O) particles, showing a great promise for a novel in situ consolidation approach to fabricate advanced Al MMCs and their net-shape components. Despite the research works exploring the SLM feasibility and processability of Al/Fe₂O₃ powder mixtures [8, 9], the in situ mechanisms with respect to various parameters such as layer thickness require further investigations.

The SLM usually involves rapid solidification (due to the short laser-material interaction time and quick movement of laser after melting). The SLM rapid solidification could modify the microstructure through microstructural refinement, solid solubility extension, and so forth. This can be particularly interesting for Al alloys where the equilibrium solid solubility of many elements is very limited [10, 11]. Therefore, the microstructural characteristic of Al MMC parts made by SLM (with a wide range of non-equilibrium phenomena) differs from those produced by conventional casting methods. These specific microstructural characteristics could lead to advanced material properties for novel net-shape MMCs components made by SLM.

The SLM process activates exothermic in situ reaction to form new constituents in the mixture of Al/Fe₂O₃ powders and simultaneously leads to rapid solidification manipulating the microstructure. The process parameters can play an important role in between. For example, the powder layer thickness can affect the heat of in situ reaction and the solidification (due to change in heat transfer condition) and subsequently the microstructure. In addition, various laser processing parameters such as laser power and scanning speed can influence the material melting and consolidation phenomena. This work has been dedicated to investigate the microstructural outcome of in situ reaction in Al/5 wt.%Fe₂O₃ powder mixture activated by SLM. Effects of laser power (), scanning speed (), and also layer thickness () on the microstructural evolution, phase changes, and material microhardness are presented and discussed.

2. Materials and Experiments

Pure Al (99.7 wt.% purity—mean particle size of 40 μm—Alpoco Ltd., UK) was mixed with 5 wt.%Fe₂O₃ powder (mean particle size of 18 μm, Inoxia Ltd., UK), as shown in Figure 1. A SLM machine (Realizer 250, MCP Ltd.) was used to process Al/5 wt.%Fe₂O₃ mixture. Argon gas was pumped into the build chamber to keep the O₂ level below 0.9%. Single layer samples were made on a thick powder bed with a laser power of 51 (W) to demonstrate thick layer thickness properties. Multilayer SLM samples with dimensions of 10 mm × 10 mm × 6 mm were fabricated onto the aluminium substrates using spot size of 0.16 mm, scan line spacing of 0.05 mm, and powder layer thicknesses of 75 μm and 50 μm. A number of multilayer samples were produced in array format with various laser powers in the range of 39–91 W and scanning speeds of 0.14 m/s and 0.5 m/s. Each layer was scanned twice. The scanning was carried out in direction for the first layer and in direction for the next layer, and so on.

Figure 1: The pure Al/5 wt.%Fe₂O₃ particle mixture.

The sample cross-sections (i.e., in the plane of one layer) were cut and polished. To reveal the microstructure, the specimens were chemically etched at room temperature using a solvent composed of 95 mL water, 2.5 mL HNO₃, 1.5 mL HCl, and 1.0 mL HF. The microstructure was viewed using a Hitachi S-3200N scanning electron microscope (SEM) equipped with an energy dispersive spectrometry (EDS) microprobe system, permitting a comparison study on alternation of chemical composition despite slight inaccuracy which might occur due to etching.

Phase identification of product was carried out using a Bruker D8 Advance X-ray diffractometer (XRD) with coupled 2Theta/Theta scan type and Cu-Kα1 radiation (wavelength 0.15406 nm). The phases were identified using the machine software (DIFFRAC.SUITE), allowing the identification of low percentage of secondary phases (i.e., weak peaks) with a high accuracy. The hardness was measured using Vickers microhardness test (100 g load was applied for 30 s) from the average of at least 5 hardness readings in conjunction with a Future-Tech Microhardness Tester FM testing machine.

3. Results

3.1. Hardness Properties

Microhardness tests were carried out to investigate the evolution of microstructural hardness with various laser powers when the multilayer parts were manufactured with layer thicknesses of 50 μm and 75 μm at two different scanning speeds ( m/s and 0.5 m/s). As shown in Figure 2, hardness usually increases with laser power, but it may reach a maximum value. For example, the hardness in the curve of  m/s and  μm increases up to about 82 W reaching a maximum value of about 53 HV and then it starts to slightly decrease with further increase of laser power. Scanning speed also affects the hardness; that is, lower scanning speed leads to higher hardness (cf. hardness curves with different scanning speeds). Moreover, thinner layer thickness of 50 μm may only have a very slight effect to enhance hardness. The highest hardness obtained in this SLM operation window belongs to the part manufactured by  W,  m/s, and  μm, which is about three times hardness value of pure aluminium (no conventionally manufactured Al composite with the comparable reinforcement characteristics was found in the literature to be used as a basis of the comparison) [12].

Figure 2: Microhardness of the multilayer parts fabricated with layer thicknesses of 50 μm and 75 μm and scanning speeds of 0.14 m/s and 0.5 m/s versus laser power.

3.2. Microstructural Characterisation and Phase Identification Using XRD

3.2.1. Single Layer Specimens Made by SLM on a Thick Powder Bed

The single layer specimens manufactured from a thick powder bed can represent a very large thickness for comparison study of various SLM layer thicknesses. Figure 3(a) exhibits a granular and integrated matrix (grain size ~5–15 μm). The EDS analysis implies that the oxygen has been efficiently removed from the Al matrix. Figure 3(b) shows the XRD pattern of the part, demonstrating that the matrix is a single Al phase.

Figure 3: (a) Typical SEM microstructural view showing a granular structure (overall chemical composition was acquired by EDS) and (b) XRD pattern of the part fabricated on a thick powder bed using  W and  m/s.

3.2.2. Multilayer Parts with Layer Thickness of 75 μm

Figures 4 and 5 show the SEM microscopic graphs of the multilayer parts (built with  μm and  W) under different laser speeds of  m/s and  m/s, respectively. Figure 4(a) exhibits grains (smooth, with a size of about 30–50 μm) surrounded by thick boundaries (appearing with a fuzzy appearance). The fuzzy appearance of boundaries may look like a coralline-like feature (the coralline tips are ~0.5 μm), as shown in Figure 4(b). The XRD results (Figure 4(c)) suggest that the part is composed of combinations such as Al, Fe²⁺Al₂O₄, and Al₁₃Fe₄ (weak peaks of Al₁₃Fe₄ indicate low content of this intermetallic). The lower scanning speed ( m/s) leads to almost the same overall microstructure (Figure 5(a)), though the thick boundaries appear coarser (the coralline tips are in an approximate range of 1-2 μm), as better demonstrated in Figure 5(b). The X-ray pattern (Figure 5(c)) showed Al and Al-Fe intermetallics such as Fe₃Al and Al₁₃Fe₄ intermetallics and Al-Fe(-O) combinations such as Fe²⁺Al₂O₄ (iron aluminium oxide), while apparent presence of Al₂O₃ was not identified.

Figure 4: (a) Overall view of microstructure, (b) higher magnification of coralline-like and fuzzy appearance of boundaries in the previous image, and (c) XRD pattern of the SLM part fabricated when  W,  m/s, and  μm.

Figure 5: (a) Overall view of microstructure, (b) boundaries seen in the previous image, and (c) XRD pattern of the part fabricated when  W,  m/s, and  μm.

The part fabricated by  W,  m/s, and  μm contains a porous and coralline-like feature propagated throughout the sample, while primary boundaries in narrow lines are recognisable (Figures 6(a) and 6(b)). The chemical composition (composing of Al and Fe with negligible content of oxygen) is in confirmation with the XRD results demonstrating Al and Al₁₃Fe₄ (Figure 6(c)). However, higher scanning speed ( m/s) even in higher laser power ( W) and scanning speed ( m/s) leads to the finer coralline-like features (in submicron sizes), as shown in Figures 7(a) and 7(b). These features are from Al₁₃Fe₄ and Fe₃Al with negligible amount of oxygen (Figures 7(b) and 7(c)).

Figure 6: (a) Microstructure, (b) the interior seen in the previous image, and (c) XRD pattern of the part fabricated when  W,  m/s, and  μm.

Figure 7: (a) Overall appearance of the grain structure, (b) higher magnification of coralline-like and fuzzy appearance in the previous image, and (c) XRD pattern of the part fabricated when  W,  m/s, and  μm.

3.2.3. Multilayer Parts with Layer Thickness of 50 μm

As shown in Figures 8(a) and 8(b), the microstructure of the parts fabricated at  W,  m/s, and  μm contains grain with a semicoralline-like feature from Al, iron aluminium oxides like AlFeO₃, and Al oxides like α-Al₂O₃ (alumina). At low scanning speed ( m/s), the homogeneous distribution of very fine particles (in nanosizes and submicron scales) within polygon grains is observed (Figures 9(a) and 9(b)). The coarser particles (~0.6–0.8 μm) form boundaries, while finer particles (~0.2-0.3 μm) are embedded inside grains (Figure 9(b)). The XRD pattern (Figure 9(c)) corresponds to Al, Fe²⁺Al₂O₄ (iron aluminium oxide), and α-Al₂O₃ (alumina). The diffraction peaks for Al₁₃Fe₄ are also detected, though the intensity is comparatively weak.

Figure 8: (a) Microstructure and (b) XRD pattern of the part made by  W,  m/s, and  μm.

Figure 9: (a) Grain structure, (b) fine particles formed inside grains and boundaries (closeup of the previous image), and (c) XRD pattern of the part made by  W,  m/s, and  μm.

By the inspection of Figures 3–9, the effect of layer thickness and laser parameters on the microstructural characteristics and identified phases can be summarised, as shown in Table 1. This will be discussed in Section 4.

Table 1: Summary of microstructural evolution in the dependence of layer thickness, laser power, and scanning speed.

Thick powder bed
 m
 m

Morphology (appearance)
Single Al phase-granular structure
Predominantly coralline-like
Semicoralline-like/particulate

Oxygen/oxide content
Least oxygen/oxide
Medium oxygen/oxide
Highest oxygen/oxide

Predominant phases
Al
Al, Al-Fe intermetallics such as Al₁₃Fe₄ and Fe₃Al; some oxides (like Fe²⁺Al₂O₄) may also be detected
Al, aluminium oxide (Al₂O₃) plus iron aluminium oxides (e.g. Fe²⁺Al₂O₄ and AlFeO₃), Al-Fe intermetallics such as Al₁₃Fe₄

Increasing laser power
N/A
Development of corallines (mainly Al-Fe intermetallics) and oxide particles from primary Al/Fe₂O₃ interface—reduction in oxygen/oxide
N/A

Lowering scanning speed
N/A
Coarsening of corallines—reduction in oxygen/oxide
Better dispersion and placement of secondary phases

4. Discussion

4.1. In Situ Interaction Initiation

Through mechanical blending, the pure aluminium (Al) and iron oxide (Fe₂O₃) powders can be uniformly distributed and fully mixed together, whilst the particles tend to adhere randomly as seen from Figure 1. This adherence is very helpful for SLM process to activate the in situ reaction between Al and Fe₂O₃ particles. In fact, in an initial stage of laser-material interaction, the energy is absorbed in a narrow layer of individual powder particles, leading to a high temperature of the surface of particles during the interaction [13, 14]. The melting/exothermic reaction starts from these interfaces between Al and iron oxide interface and the thermite reaction progresses regarding the following stoichiometric equation:

The final phases, Al₂O₃ and Fe₃Al intermetallics, are formed by an in situ chemical reaction in which Al reduces the iron oxide [15, 16]. The extra heat from in situ reaction facilitates melting during SLM process. The mechanism of reaction involves reducing Fe₂O₃ to Fe₃O₄ and FeO by releasing the oxygen and Al oxidation, interaction of Al with iron oxides, and formation of phases such as iron-aluminium-oxide, alumina, iron, and Al-Fe intermetallics, depending on reaction temperature and Fe₂O₃/Al ratios [17, 18].

4.2. Effect of Layer Thickness, Laser Power, and Scanning Speed on Oxide Formation

The oxygen content as the main factor for quantity of oxides is significantly altered according to the parameters used to manufacture parts. This can be attributed to relation of oxide formation with temperature. The increased reaction temperature (due to higher laser power) and inert atmosphere lead to the decomposition of Fe₂O₃ into FeO and Fe and oxygen which escapes from the specimen [18]. In a parallel manner, the vaporisation of thin oxide films to fume can occur on the top of the Al molten pool in high temperatures of laser/material interaction [5]. The released oxygen and oxide film fume can be carried away by the inert gas flowing over the bed [19]. The Marangoni forces can contribute to this oxygen removal by stirring and breaking oxides [5]. On this basis, higher laser power and lower scanning speed (leading to higher temperatures) should contribute to oxygen removal by intensifying the melting flow, decomposition, and evaporation [5, 18]. For example, low scanning speed of 0.14 m/s in Figure 5 results in lower comparative oxygen than that of Figure 4 ( m/s).

As observed from Figures 8 and 9 ( μm) to Figures 4–7 ( μm) and Figure 3 (thick powder bed), the higher oxygen appears in lower layer thickness. This is because the thicker layer thickness reduces the oxygen by enhancing temperature and stirring (since a thicker layer reduces the cooling rate, activates more exothermic reaction and produces a larger melting pool). The higher oxygen contributes to the formation of hard oxides such as aluminium oxide (Al₂O₃) or iron aluminium oxides (like Fe²⁺Al₂O₄ and AlFeO₃), reinforcing the matrix.

4.3. Microstructures, Phases, and Microhardness

The single Al phase granular feature (Figure 3), formed in the SLM specimen built on a thick Al/Fe₂O₃ powder bed, can be attributed to enhanced oxygen removal at large layer thickness. This leads to an Al matrix saturated by Fe (SLM rapid solidification from high temperatures assists saturation of Al by other elements [11, 20]). This contributes to strengthening by solution hardening.

The multilayer parts exhibit higher microhardness than that of the conventional pure aluminium (Figure 2). The lowest hardness belongs to Figure 4 in which fuzzy and coralline-like boundaries have just started to develop into interior. These phases are Al-Fe intermetallics and Al(-Fe) oxides, demanded for hardening/strengthening purposes (e.g., Al oxide has been used as reinforcement in Al alloys [21] or Al₁₃Fe₄ has been recognised as major hardening phase in surface hardening of Al by Fe-ion implantation [22]). Therefore, they start to enhance the hardness of Al matrix compared to pure Al. Considering the detected combinations, Al₁₃Fe₄ (equilibrium) is a result of transition from Fe₃Al (the ordinary production of (1)) due to excessive Al [23]. Also, Fe²⁺Al₂O₄ has been formed due to its lower activation energy than that of Al₂O₃ [15], though it tends to transform into Al₂O₃ and Al-Fe intermetallics [18].

The average particle size of Al powders (about 40 μm) results in a similar range of grain size in Figure 4(a). Higher laser power of 82 W develops coralline-like feature (Figure 7) from ultrafine intermetallics such as Al₁₃Fe₄ and Fe₃Al (Figure 7(c)). This is accompanied with removing oxides from matrix and lowering the oxygen content (Figures 7(b) and 7(c)). Despite the absence of oxides, the fine and hard Al-Fe intermetallics enhance the hardness (see the corresponding microhardness curve in Figure 2).

Both Figures 4 and 5 contain coralline-like features in boundaries, however the corallines in Figure 5 are slightly further developed due to lower scanning speed. In fact, lower laser speed enhances the laser input and decreases the cooling rate leading to coarser corallines (the coralline tips are ~1-2 μm in Figure 5, but ~0.5 μm in Figure 4). Despite the coarsening effect, enhancing the melting (by increasing laser input) results in further propagation of these Al-Fe intermetallics into interior, a more uniform microstructure, and a higher hardness. This completes in higher laser powers (Figure 6), leading to the highest hardness of the relevant curve (treated at  W,  m/s, and  μm—Figure 2). After this, the hardness may fall despite the bonding improvement, perhaps due to the excessive coarsening or formation of other softer in situ products.

Decreasing the layer thickness of the parts to 50 μm changes the sharp-pointed coralline-like appearance of microstructure (Figure 7) into semicorallines and particles (Figures 8 and 9). The oxygen content is considerably higher than what was observed in higher layer thickness (e.g., cf. Figures 8 to 7), increasing the oxide particles.

Reducing the laser speed in conjunction with lower layer thickness of 50 μm (Figures 9(a) and 9(b)) leads to uniform distribution of very fine particles (in nanosize and submicron scale) with strong bonding within the matrix. This results in the highest hardness (Figure 2). Formation of these reinforcing particles can be attributed to the used parameters. In fact, the lower layer thickness intensifies fragmentation of corallines (by remelting the ex-layers), refines the microstructure (by increasing the cooling rate), and increases the oxide particles (by restricting the oxygen removal). Besides, the lower laser speed contributes to making particles by assisting the oxide fragmentation.

4.4. In Situ Combined SLM Phenomena

The Al-Fe equilibrium binary diagram shows a eutectic point around 1.8 wt.% iron which is composed of Al and Al₃Fe (Al₁₃Fe₄) [23, 24]. The eutectics usually tend to form with a lath-like morphology, but, here, the rapid solidification restricts their growth. Thus, these incomplete Al-Fe lath-like eutectics appear with a coralline-like morphology in areas with low oxygen content (e.g., Figure 7(b)). The existence of coralline-like phases has rarely been reported by other researchers. For example, Wong et al. [20] observed that the eutectic silicon in Al-Si alloys was strongly modified during laser treatment, in such a manner that silicon crystal in eutectic was changed morphologically from lath-like into coralline-like.

As summarised in Table 1, the SLM of single layer specimens on a thick powder bed forms an Al granular feature saturated by Fe. When the 75 μm layer thickness is used, low laser energies form the coralline-like phases (being in fact rapidly solidified Al-Fe eutectics), though Al oxide (mainly in the form of particles) may also be found from surface oxide fragmentations or in situ products. Higher laser power develops the in situ reaction leading to incorporation of Al into Fe²⁺Al₂O₄ and transforming it into Fe₃Al and then equilibrium Al₁₃Fe₄ (as much as possible depending on the condition). Simultaneously, oxygen removal is adequate to mitigate the oxides, leaving mainly Al and Al-Fe intermetallics. Thus, coralline-like features propagate all over the samples in these conditions. A decrease in layer thickness into 50 μm suppresses the oxygen removal and increases the stable and particulate Al₂O₃. It also increases the solidification rate which decreases the transformation of iron aluminium oxides (like Fe²⁺Al₂O₄ and AlFeO₃) into intermetallics. The lower scanning speed may increase the fragmentation of oxide layers. This collaborates with the ex-layer remelting which breaks the corallines formed in previous layers. Consequently, coralline-like appearance may disappear and particulate reinforced Al matrix may be revealed.

5. Conclusions

(i)In situ reaction was successfully activated by using SLM process in a powder mixture of Al/5 wt.%Fe₂O₃. The microstructural evolution of SLM parts was investigated in the dependence of various parameters such as powder, layer thickness, laser power and scanning speed.(ii)Thicker layers lead to more efficient oxygen removal during SLM. This can be considered as the main reason for the large microstructural differences with changing the layer thickness.(iii)The microstructure after SLM of a thick powder bed, 75 μm layer thickness, and 50 μm layer thickness appeared with dominantly granular, coralline-like (being in fact rapidly laser solidified Al-Fe eutectics), and coralline-particulate and particulate features, respectively. These microstructures represent mainly pure Al, Al-Fe intermetallics (such as Fe₃Al and Al₁₃Fe₄), and Al(-Fe)-O oxides (such as Al₂O₃, Fe²⁺Al₂O₄, and AlFeO₃) after rapid solidification.(iv)The earliest in situ products are phases such as Fe₃Al and Al(-Fe)-O oxides (e.g., Fe²⁺Al₂O₄), but they tend to transform into more stable combinations such as Al₁₃Fe₄ and α-Al₂O₃.(v)Higher laser power also contributes to more efficient oxygen removal during SLM. Higher scanning speed leads to finer Al-Fe coralline-like features, and it may restrict the in situ progress and transformation of products.(vi)A very promising result (useful to manufacture Al matrix composites) was achieved by using low layer thickness, high laser power, and low scanning speed. This led to well-bonded and uniform distribution of fine, hard, and stable particles in Al matrix and consequently resulted in the highest comparative microhardness.

Conflict of Interests

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

References

P. S. Mohanty and J. Mazumder, “Solidification behavior and microstructural evolution during laser beam-material interaction,” Metallurgical and Materials Transactions B, vol. 29, no. 6, pp. 1269–1279, 1998.

S. Dadbakhsh, L. Hao, and N. Sewell, “Effect of selective laser melting layout on the quality of stainless steel parts,” Rapid Prototyping Journal, vol. 18, no. 3, pp. 241–249, 2012.

J.-P. Kruth, G. Levy, F. Klocke, and T. H. C. Childs, “Consolidation phenomena in laser and powder-bed based layered manufacturing,” CIRP Annals, vol. 56, no. 2, pp. 730–759, 2007.

E. C. Santos, M. Shiomi, K. Osakada, and T. Laoui, “Rapid manufacturing of metal components by laser forming,” International Journal of Machine Tools and Manufacture, vol. 46, no. 12-13, pp. 1459–1468, 2006.

E. Louvis, P. Fox, and C. J. Sutcliffe, “Selective laser melting of aluminium components,” Journal of Materials Processing Technology, vol. 211, no. 2, pp. 275–284, 2011.

D. Buchbinder, H. Schleifenbaum, S. Heidrich, W. Meiners, and J. Bültmann, “High power selective laser melting (HP SLM) of aluminum parts,” Physics Procedia A, vol. 12, pp. 271–278, 2011.

L. Hao and S. Dadbakhsh, “Materials and process aspects of selective laser melting of metals and metal matrix composites: a review,” Chinese Journal of Lasers, vol. 36, no. 12, pp. 3192–3203, 2009.

S. Dadbakhsh and L. Hao, “In situ formation of particle reinforced Al matrix composite by selective laser melting of Al/Fe₂O₃ powder mixture,” Advanced Engineering Materials, vol. 14, no. 1-2, pp. 45–48, 2012.

S. Dadbakhsh, L. Hao, P. G. E. Jerrard, and D. Z. Zhang, “Experimental investigation on selective laser melting behaviour and processing windows of in situ reacted Al/Fe₂O₃ powder mixture,” Powder Technology, vol. 231, pp. 112–121, 2012.

E. J. Lavernia and T. S. Srivatsan, “The rapid solidification processing of materials: science, principles, technology, advances, and applications,” Journal of Materials Science, vol. 45, no. 2, pp. 287–325, 2010.

M. Rajabi, M. Vahidi, A. Simchi, and P. Davami, “Effect of rapid solidification on the microstructure and mechanical properties of hot-pressed Al-20Si-5Fe alloys,” Materials Characterization, vol. 60, no. 11, pp. 1370–1381, 2009.

ASM International Handbook Committee, vol. 2 of Properties and Selection: Nonferrous Alloys and Special-Purpose Materials, American Society for Metals (ASM) International, Metals Park, Ohio, USA, 1992.

P. Fischer, V. Romano, H. P. Weber, N. P. Karapatis, E. Boillat, and R. Glardon, “Sintering of commercially pure titanium powder with a Nd:YAG laser source,” Acta Materialia, vol. 51, no. 6, pp. 1651–1662, 2003.

D. Gu, Z. Wang, Y. Shen, Q. Li, and Y. Li, “In-situ TiC particle reinforced Ti-Al matrix composites: powder preparation by mechanical alloying and Selective Laser Melting behavior,” Applied Surface Science, vol. 255, no. 22, pp. 9230–9240, 2009.

R.-H. Fan, H.-L. Lü, K.-N. Sun, W.-X. Wang, and X.-B. Yi, “Kinetics of thermite reaction in Al-Fe₂O₃ system,” Thermochimica Acta, vol. 440, no. 2, pp. 129–131, 2006.

J. Yang, P. La, W. Liu, and Y. Hao, “Microstructure and properties of Fe₃Al-Fe₃ AlC0.5 composites prepared by self-propagating high temperature synthesis casting,” Materials Science and Engineering A, vol. 382, no. 1-2, pp. 8–14, 2004.

L. Durães, B. F. O. Costa, R. Santos, A. Correia, J. Campos, and A. Portugal, “Fe₂O₃/aluminum thermite reaction intermediate and final products characterization,” Materials Science and Engineering A, vol. 465, no. 1-2, pp. 199–210, 2007.

J. Mei, R. D. Halldearn, and P. Xiao, “Mechanisms of the aluminium-iron oxide thermite reaction,” Scripta Materialia, vol. 41, no. 5, pp. 541–548, 1999.

F. Verhaeghe, T. Craeghs, J. Heulens, and L. Pandelaers, “A pragmatic model for selective laser melting with evaporation,” Acta Materialia, vol. 57, no. 20, pp. 6006–6012, 2009.

T. T. Wong, G. Y. Liang, and C. Y. Tang, “The surface character and substructure of aluminium alloys by laser-melting treatment,” Journal of Materials Processing Technology, vol. 66, no. 1–3, pp. 172–178, 1997.

G. Dirras, J. Gubicza, D. Tingaud, and S. Billard, “Microstructure of Al-Al₂O₃ nanocomposite formed by in situ phase transformation during Al nanopowder consolidation,” Materials Chemistry and Physics, vol. 129, no. 3, pp. 846–852, 2011.

K. Y. Gao and B. X. Liu, “Surface hardening of Al by high current Fe-ion implantation,” Journal of Applied Physics, vol. 82, no. 5, pp. 2209–2214, 1997.

Á. Griger and V. Stefániay, “Equilibrium and non-equilibrium intermetallic phases in Al-Fe and Al-Fe-Si Alloys,” Journal of Materials Science, vol. 31, no. 24, pp. 6645–6652, 1996.

C. M. Allen, K. A. Q. O'Reilly, and B. Cantor, “Effect of semisolid microstructure on solidified phase content in 1xxx Al alloys,” Acta Materialia, vol. 49, no. 9, pp. 1549–1563, 2001.