Journal of NanomaterialsVolume 2011 (2011), Article ID 793135, 5 pagesdoi:10.1155/2011/793135

Research Article

Mechanochemical Synthesis and Rapid Consolidation of Nanocrystalline 3NiAl- Composites

In-Jin Shon,1,2 In-Yong Ko,¹ Seung-Hoon Jo,¹ Jung-Mann Doh,³ Jin-Kook Yoon,³ and Sang-Whan Park³

¹Division of Advanced Materials Engineering and Research Center of Advanced Materials Development, Engineering College, Chonbuk National University, Chonbuk 561-756, Republic of Korea²Department of Hydrogen and Fuel Cells Engineering, Specialized Graduate School, Chonbuk National University, Chonbuk 561-756, Republic of Korea³Advanced Functional Materials Research Center, Korea Institute of Science and Technology, P.O. Box 131, Cheongryang, Seoul 130-650, Republic of Korea

Received 20 July 2011; Accepted 30 September 2011

Academic Editor: Claude Estournes

Copyright © 2011 In-Jin Shon et al. 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.

Nanopowders of 3NiAl and Al₂O₃ were synthesized from 3NiO and 5Al powders by high-energy ball milling. Nanocrystalline Al₂O₃ reinforced composite was consolidated by high-frequency induction-heated sintering within 3 minutes from mechanochemically synthesized powders of Al₂O₃ and 3NiAl. The advantage of this process is that it allows very quick densification to near theoretical density and inhibition grain growth. Nanocrystalline materials have received much attention as advanced engineering materials with improved physical and mechanical properties. The relative density of the composite was 97%. The average Vickers hardness and fracture toughness values obtained were 804 kg/mm² and 7.5 , respectively.

1. Introduction

NiAl has a high melting temperature (1711 K), good thermal conductivity (75 W/mK), low raw material cost, good oxidation resistance, and low density (5.91 g/cm³). These properties make NiAl a promising candidate for use in the aircraft and automotive industries [1]. However, like many intermetallics, use of NiAl in industry has been limited due to low fracture toughness, around 5.4 MPa m−1/2 and a low hardness of about 430 HV [1–3]. The mechanical properties can be improved significantly by reinforcing NiAl with hard ceramic particles such as Al₂O₃ [3] and by fabrication of nanostructured composite [4]. Al₂O₃ has a density of 3.98 g/cm³, a Youngs’ modulus of 380 GPa, excellent oxidation resistance and good high-temperature mechanical properties [5]. Hence, a microstructure consisting of NiAl and Al₂O₃ may have sufficient oxidation resistance and high-temperature mechanical properties to be a successful high-temperature structural material. NiAl composites have been prepared by several methods, including high-energy ball milling, pressureless sintering, and pulse plasma sintering [3, 6].

Nanocrystalline powders were recently developed by such thermochemical and thermomechanical processes as the spray conversion process (SCP), coprecipitation, and high-energy milling [7–9]. However, the grain sizes in sintered materials become much larger than in presintered powders due to fast grain growth during conventional sintering. Therefore, even though the initial particle size is less than 100 nm, grain size increases rapidly up to 2 μm or larger during conventional sintering [10]. Controlling grain growth during sintering is one of the keys to the commercial success of nanostructured materials. High-frequency induction-heated sintering, which can yield dense materials within 2 min, is effective for controlling grain growth [11, 12].

The purpose of this work is to produce dense nanocrystalline 3NiAl-Al₂O₃ composite within 3 minutes from mechanically synthesized powders using high-frequency induction-heated sintering and to evaluate its mechanical properties (hardness and fracture toughness).

2. Experimental Procedures

Powders of 99.9% NiO (−325 mesh, Alfa) and 99% pure Al (−325 mesh, Cerac, Inc.) were used as starting materials. 3NiO and 5Al powder mixtures were first milled in a high-energy ball mill, a Pulverisette-5 planetary mill, at 250 rpm for 10 h. Tungsten carbide balls (8 mm in diameter) were used in a sealed cylindrical stainless steel vial under an argon atmosphere. The weight ratio of ball to powder was 30 : 1. Milling resulted in a significant reduction in grain size.

The grain sizes of NiAl and Al₂O₃ were calculated by Suryanarayana and Grant Norton’s formula [13]: where is the full width at half-maximum (FWHM) of the diffraction peak after instrument correction, and are FWHM caused by small grain size and internal stress, respectively, is constant (with a value of 0.9), is the wavelength of the X-ray radiation, and are grain size and internal strain, respectively, and is the Bragg angle. The parameters B and follow Cauchy’s form with the relationship: , where and are the FWHM of the broadened Bragg peaks and the standard sample’s Bragg peaks, respectively.

After milling, the mixed powders were placed in a graphite die (outside diameter, 45 mm; inside diameter, 20 mm; height, 40 mm) and then introduced into the high-frequency induction-heated sintering system made by Eltek in South Korea, shown schematically in reference [11, 12]. The four major stages in the synthesis are as follows. Stage 1: evacuation of the system; stage 2: application of uniaxial pressure; stage 3: heating of sample by induced current; stage 4: cooling of sample. Temperatures were measured by a pyrometer focused on the surface of the graphite die. The process was carried out under a vacuum of 40 mTorr.

The relative densities of the synthesized sample were measured by the Archimedes method. Microstructural information was obtained from product samples that were polished at room temperature. Compositional and microstructural analyses of the products were completed through X-ray diffraction (XRD) and scanning electron microscopy (SEM) with energy dispersive X-ray analysis (EDAX). Vickers hardness was measured by performing indentations at a load of 50 kg and a dwell time of 15 s on the sintered samples.

3. Results and Discussion

The interaction between 3NiO and 5Al, that is, is thermodynamically favorable.

X-ray diffraction results of high-energy ball-milled powders and sintered specimens are shown in Figures 1(a) and 1(b). The reactant powders of NiO and Al were not detected in Figure 1(a) but products, NiAl and Al₂O₃, were detected. From the above result, the mechanochemical synthesis occurs completely during the high-energy ball milling. Figure 2 shows a plot of versus of NiAl and Al₂O₃ in milled powders. The average grain sizes of NiAl and Al₂O₃ measured by Suryanarayana and Grant Norton’s formula are about 9 nm and 26 nm, respectively. The variations in shrinkage displacement and temperature of the surface of the graphite die with heating time during processing of NiAl and Al₂O₃ systems are shown in Figure 3. As the induced current was applied, thermal expansion occurred and then the shrinkage displacement abruptly increased at about 900°C.

(a)

(b)

Figure 1: XRD patterns of mechanically synthesized powder (a) and sintered specimen.

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(b)

Figure 2: Plot of versus for NiAl (a) and Al₂O3 (b) in mechanically milled powders.

Figure 3: Variation in temperature and shrinkage displacement with heating time during high-frequency induction-heated sintering of 3NiAl + Al₂O₃.

Figure 4 shows the FE-SEM image and EDS analysis of NiAl-Al₂O₃ composites sintered at 1100°C. The relative density of NiAl-Al₂O₃ composites is about 97%. The NiAl-Al₂O₃ composites consist of nanocrystallites. In EDS, Al, Ni, and O peaks are detected and heavier contaminants, such as W and Fe from a ball or milling container, were not detected. Figure 5 shows a plot of versus of NiAl and Al₂O₃ in sintered composite. The structure parameters, that is, the average grain sizes of NiAl and Al₂O₃ obtained from the X-ray data by Suryanarayana and Grant Norton’s formula, were 43 nm and 69 nm, respectively. The average grain sizes of the sintered NiAl and Al₂O₃ were not significantly larger than the grain sizes of the initial powders, indicating the absence of significant grain growth during sintering. This retention of the grain size is attributed to the high heating rate and the relatively short exposure of the powders to the high temperature. The role of current in sintering has been the focus of several attempts to explain the observed enhancement of sintering and the improved characteristics of the products. The role played by the current has been hypothesized to involve a fast heating rate due to Joules heating, the presence of plasma in pores separating powder particles, and the intrinsic contribution of the current to mass transport [14–17].

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(b)

Figure 4: FE-SEM image and EDS of 3NiAl-Al₂O₃ composites heated to 1100°C.

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(b)

Figure 5: Plot of versus for NiAl (a) and Al₂O₃ (b) in sintered composite.

Vickers hardness measurements were made on polished sections of the 3NiAl-Al₂O₃ composite using a 50 kgfload and 15 s dwell time. The calculated hardness value of 3NiAl-Al₂O₃ composite was 804 kg/mm². This value represents an average of five measurements. Indentations with large enough loads produced median cracks around the indent. From the lengths of these cracks, fracture toughness values can be determined using an expression proposed by Anstis et al. [18]: where is Young’s modulus, is the indentation hardness, is the indentation load, and is the trace length of the crack measured from the center of the indentation. The modulus was estimated by the rule of mixtures for a 0.37 volume fraction of Al₂O₃ and 0.63 volume fraction of NiAl using (Al₂O₃) = 380 GPa [5] and (NiAl) = 193 GPa [19].

As in the case of hardness values, the toughness values were derived from the average of five measurements. The toughness value obtained by the method of calculation is 7.5 MPa·m1/2. A typical indentation pattern for the NiAl-Al₂O₃ composite is shown in Figure 6(a). Typically, one to three additional cracks were observed to propagate from the indentation corner. A higher magnification view of the indentation median crack in the composite is shown in Figure 6(b). This shows that the crack propagates deflectively . The hardness and fracture toughness of NiAl are reported as 430 kg/mm² and 5.4 MPa·m1/2, respectively [3]. Not only the hardness but also the fracture toughness of 3Ni-Al₂O₃ composites is higher than that of monolithic NiAl due to addition of hard phase of Al₂O₃ and crack deflection by Al₂O₃.

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(b)

Figure 6: (a) Vickers hardness indentation and (b) median crack propagation in the NiAl-Al₂O₃ composite.

4. Conclusions

Nanopowders of NiAl and Al₂O₃ are synthesized from 3NiO and 5Al powders by high-energy ball milling. Using the high-frequency induction-heated sintering method, the densification of nanocrystalline Al₂O₃-reinforced NiAl composites were accomplished from mechanochemically synthesized powders. Complete densification can be achieved within 3 minutes. The relative density of the composite was 97% for an applied pressure of 80 MPa and an induced current. The average grain sizes of NiAl and Al₂O₃ prepared by HFIHS were about 43 nm and 69 nm, respectively. The average hardness and fracture toughness values obtained were 804 kg/mm² and 7.5 MPa·m1/2, respectively. Not only the hardness but also the fracture toughness of 3NiAl-Al₂O₃ composites is higher than that of monolithic NiAl due to addition of hard phase of Al₂O₃ and crack deflection by Al₂O₃.

Acknowledgments

This work was supported by the New and Renewable Energy R&D Program (2009T00100316) of the Ministry of Knowledge Economy, Republic of Korea.

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