Enhancement of the fracture toughness of bulk L12-based (Al+12.5 at.% M)3Zr (M=Cu, Mn) intermetallics synthesized by mechanical alloying
Introduction
The L12-ordered cubic zirconium trialuminides are derived from tetragonal D023-ordered Al3Zr by alloying with fourth-period transition elements such as Cr, Mn, Fe, Ni, Cu, and Zn. They have been considered as advanced high temperature structural materials because of their high melting temperature, low density and good oxidation resistance [1], [2], [3], [4], [5], [6]. The major problems limiting the practical use of this compound are, however, the low ductility and fracture toughness at ambient temperature and poor strength at ambient and elevated temperatures [7]. Recently, research efforts have been made to improve the ductility of Al3X intermetallic compounds. Nanocrystallization is expected to improve their ductilities by enhancing grain boundary sliding and diffusion creep at room temperatures [4]. The modification of crystal structure from the tetragonal D022/D023 to the more symmetric cubic L12 structure is also known to improve their ductilities to some extent. It is, therefore, expected that the ductility of nanocrystalline L12 Al3X intermetallic compound is considerably enhanced [8]. However, L12 structure does not guarantee a ductile behavior [9] and the experiments showed that ductilities are disappointingly low, typically less than 2% elongation for most nanostructured materials such as L12 Al3Zr and Al3Ti alloy with grain sizes <25 nm [10]. One of the reasons that L12 alloys are brittle might be the antiphase boundary (APB)-coupled dislocation slip. It has been observed that 〈110〉 dislocations in L12-stabilized TiAl3 alloys dissociate into APB coupled with two 〈110〉/2 superpartials [11], [12]. Consequently, the nucleation of dissociations from the crack tip in these alloys is difficult and they should be intrinsically brittle. According to Koch [10], three major limitations to ductility for nanocrystalline materials can be identified: (1) artifacts from processing; (2) force instability in tension; (3) crack nucleation or propagation instability. Therefore, annealing for the L12-based bulk zirconium trialuminides with nanocrystalline structure may be necessary to improve fracture toughness by increasing grain size.
In our previous study [13], after annealing the L12 bulk (Al+12.5 at.% Cu)3Zr specimen with nanocrystalline structure in the temperature range, 500–1200 °C for 2 h, the fracture toughness increased up to 4.6 MPam1/2, accompanied with increase in the grain size (∼100 nm). It is generally known that fracture toughness increases as the grain size decreases down to the micro-sized range [14], [15], but the effect of grain size on fracture toughness is controversial in the nano-sized range. The results of the consolidated bulk specimens do not show an explicit relationship between grain size and fracture toughness in the nano-scale. The micro-hardness increased up to 1010 Hv following the Hall–Petch relationship as the grain size decreased down to a critical value (41.7 nm), but further decrease in the grain size caused a decrease in the hardness. On the other hand, the L12 structure of bulk specimen began to transform to the D023 structure at 900 °C because it is thermally metastable. Furthermore, Pope [16] have reported that Mn can increase the cleavage resistance because Mn elements segregate at the grain boundaries, resulting in an increase of the grain boundary cohesion. In the present study, 12.5 at.% Mn as well as 12.5 at.% Cu added Al3Zr intermetallic compounds was synthesized by PBM (planetary ball milling) and SPS (spark plasma sintering). Moreover, it is generally known that the micro-alloying with boron sharply increases the ductility (or fracture toughness) and effectively suppresses intergranular or cleavage fracture [17], [18], [19].
Thus, the purpose of the present study is to enhance the fracture toughness by means of annealing and boron addition in bulk (Al+12.5 at.% M)3Zr (M=Cu, Mn) specimens. Furthermore, to examine the effect of grain size on the fracture toughness in nano-sized level, we tried to synthesize bulk specimen by arc melting milled powders.
Section snippets
Planetary ball milling (PBM)
The elemental powders of aluminum (−325 mesh, 99.5% pure) and zirconium (−325 mesh, 99.9% pure) were used as starting materials to prepare Al-25 at.% Zr alloys. 12.5 at.% of Cu and Mn (−150 mesh, 99.5% pure), respectively, as ternary elements were added to synthesize the (Al+12.5 at.% M)3Zr (M=Cu, Mn) alloys. Boron (−325 mesh, 99.0% pure) was added at content levels of 0.001 wt% (10 ppm) to 1 wt% (104 ppm). It is generally reported that boron is soluble up to 0.1 wt% (103 ppm), and high boron
The microstructure and mechanical properties of the bulk specimens annealed
In the bulk (Al+12.5 at.% Mn)3Zr specimens annealed, the L12 phase was maintained up to 1000 °C and began to transform to D023 phase at 1100 °C, as shown in Table 1. The micro-hardness as sintered state was 983.9 Hv. The bulk specimens annealed over 1100 °C consisted of L12 and D023. As the annealing temperature increased up to 1200 °C, the grain size increased up to 98.7 nm. The fracture toughness increased as the grain size increased. This relationship between grain size and mechanical properties
Conclusions
(1) The fracture toughness of the SPS-processed L12-type bulk (Al+12.5 at.% Cu)3Zr specimens which had the smallest grain size (<10 nm) showed the lowest value of 1.54 MPam1/2, irrespective of the constituent phase (L12 or D023). In the bulk L12 (Al+12.5 at.% M)3Zr (M=Cu, Mn) specimens annealed at the temperature range 500–1200 °C for 2 h, the L12 phase began to transform to D023 phase at 900 and 1100 °C, respectively. The fracture toughness increased up to 4.4–4.6 MPam1/2 as the grain size increased
Acknowledgements
This study was supported by grant No. [R01-1998-000-00040-0] from the Basic Research Program of the Korea Science and Engineering Foundation and by Brain Korea 21 project.
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