To investigate the impact of various Al-Ti-B grain-refiners on solidification and grain-refining performance, a wrought aluminium alloy AA6182 was used. Three different grain-refiners from different manufacturers were used to establish the efficiency, i.e. contact time before casting, on the primary solidification and grain formation size. The primary solidification of α-Al grains at inoculation was observed by using thermal analysis (TA). Differential scanning calorimetry (DSC) was used in order to analyze the quality of various grain-refiners. The size of the primary grains was analyzed using optical microscopy (OM). Scanning electron microscopy (SEM) was used to estimate the size and distribution of Al3Ti and TiB2 particles in various grain-refiners and to establish the best efficiency of the investigated grain-refiners.
Within 1-4 min of inoculation the smallest fine equiaxed grains were achieved when either one of the investigated grain-refiners was added. It was established, that grain-refiner A contains higher content of impurities which do not melt in the experimental temperature range made by DSC method. The most pure grain-refiner turned out to be grain-refiner B, in which the most optimal number of TiB2 particles and particle size distribution was found.
In this study, Fe-40wt% TiB2 nanocomposite powders were fabricated by two different methods: (1) conventional powder metallurgical process by simple high-energy ball-milling of Fe and TiB2 elemental powders (ex-situ method) and (2) high-energy ball-milling of the powder mixture of (FeB+TiH2) followed by reaction synthesis at high temperature (in-situ method). The ex-situ powder was prepared by planetary ball-milling at 700 rpm for 2 h under an Ar-gas atmosphere. The in-situ powder was prepared under the same milling condition and heat-treated at 900oC for 2 h under flowing argon gas in a tube furnace to form TiB2 particulates through a reaction between FeB and Ti. Both Fe-TiB2 composite powder compacts were sintered by a spark-plasma sintering (SPS) process. Sintering was performed at 1150℃ for the ex-situ powder compact and at 1080℃ for the in-situ powder for 10 minutes under 50 MPa of sintering pressure and 0.1 Pa vacuum for both processes. The heating rate was 50o/min to reach the sintering temperature. Results from analysis of shrinkage and microstructural observation showed that the in-situ composite powder compacts had a homogeneous and fine microstructure compared to the ex-situ preparation, even though the sintered densities were almost the same (99.6 and 99.8% relative density, respectively).