Open Journal of Metal
Vol.04 No.03(2014), Article ID:49202,6 pages

Investigation on Microstructure and Grain Refining Performance of a New Type of Al-3Ti-1C Master Alloy

Vahid Hassanbeygi, Ali Shafyei

Department of Materials Engineering, Isfahan University of Technology, Isfahan, Iran


Copyright © 2014 by authors and Scientific Research Publishing Inc.

This work is licensed under the Creative Commons Attribution International License (CC BY).

Received 13 June 2014; revised 14 July 2014; accepted 12 August 2014


Grain refining process plays a significant role in preventing columnar and coarse grains and it encourages fine grain formation. Although Al-Ti-B master alloys use widely as aluminium grain refiners, there are several problems in their applications. So, this kind of master alloys use less than last. Because of great properties of Al-Ti-C refiners, they can be considered as suitable candidates for use instead of Al-Ti-B master alloys. In recent years, Al-Ti-C refiners have attracted huge atten- tion among researchers. In this paper, Al-3Ti-1C master alloy is prepared with a melting reaction method. This method involves adding graphite powder and fine titanium particles into super- heated pure aluminium. Then microstructure of this master alloy is studied by scanning electron microscope (SEM) and its phases are distinguished by energy dispersive spectroscopy (EDS). In the next part, 200 ppm of Al-3Ti-1C master alloy is added to pure aluminium and its refining efficiency is compared with the condition in which TiC powders are added to aluminium melt directly. It is found that the fading time for both Al-3Ti-1C and TiC powder is about 15 minutes and in overall, grain refining efficiency of Al-3Ti-1C is more than TiC powders in 60 minutes.


Al-Ti-C Master Alloy, Grain Size, Microstructure, Grain Refining, TiC Powder

1. Introduction

Grain refinement is an important technique to improve the soundness of aluminium products. Usually, master alloys add to molten metal as a grain refiner. They contain potent nucleant particles. These particles promote formation of a fine equiaxed macrostructures. The fine and equiaxed grain structure causes high toughness, high yield strength, excellent formability, good surface finish and improve ability to achieve a uniform anodized surface, better fatigue life and good machinability. Furthermore, a sound grain refining practice avoids hot tearing, allows a marked increase in casting speed and improves the homogeneity of cast structures by refining the distribution of secondary phases and micro porosity [1] - [6] .

A lot of inactive particles are found on grain boundaries, where they have been pushed in front of the solid- liquid interface, whereas active particles are found within grains [5] . In aluminium master alloys, usually TiC and TiB2 particles are nucleant and TiAl3 particles restrict the growth of α-Al grains after they are nucleated [7] . So, fine TiAl3 particles are good [8] [9] but these particles dissolve in melt rapidly and don’t have a favorable fading behavior [10] . Usually, TiAl3 phases are blocky and these blocky crystals tend to act fast, but their effects fade quickly. Sometimes TiAl3 phases have petal and plate-like structures and act more slowly, but their grain refining efficiency improves with time and lasts longer [11] .

Mohanty and Gruzleski studied on Al-Ti-B master alloys and conclude that TiB2 is a poor nucleant but, it is well known that the Al-Ti-C master alloys are good refiners for Al alloys [8] . The TiC particles, present in the master alloy, remain stable in the melt and act as the active nucleant substrates. These particles are very fine and act fast but dissolve in molten aluminium rapidly. So, to improve the fading time, coarse TiAl3 particles are preferable.

The particle theory suggests that the nucleation occurs on the carbides within the master alloys [12] .

The initial temperature of melt has a big effect on the reaction delay time. The lowest temperature of melt resulted in the longest delay time [13] [14] .

Maxwell and Hellawell [15] suggest that the time for complete dissolution of the aluminide, being highly dependent on the size of the aluminide. In fact, proportional to the square of the particles dimension:


where t is the time for complete dissolution of the aluminides and D is particle size (µm). They did not mention the temperature for the analysis.

2. Experimental Procedure

Al-Ti-C master alloys were produced from Ti powder; commercial pure Al and graphite powder with size less than 250 µm. Master alloys were prepared by a melt reaction method. In this method, commercial pure Al melted using a resistance furnace with argon protective atmosphere. When the melt temperature reached to 1200˚C, graphite and fine titanium particles added into it. The holding time was 60 min with stirring the melt every 15 minutes. Then, melt was poured into a 500˚C preheated permanent mould. A k-type thermocouple was mounted and placed in the center of mould. The cooling rate in the mould was calculated with using a data acquisition system.

The efficiency of produced Al-3Ti-1C master alloy on grain refining, was evaluated by adding 200 ppm of master alloy into the pure molten Al at 720˚C. The holding time was variable, from 5 to 120 minutes. Then, the melt poured into a permanent mould. The samples cut at a distance of 35 mm from the bottom surface and prepared for micro or macrostructure tests.

Also, the TiC powder with size less than 100 µm was added into molten Al as a grain refiner and the results compared with Al-3Ti-1C master alloy. Figure 1 shows the SEM picture of TiC powders.

3. Results and Discussions

The cooling rate diagram shows that the solidification of master alloy is fast. The solidification complete within 130 seconds (Figure 2) and maximum cooling rate, according to the first derivative of this diagram, is 5˚C/s.

Figure 3 shows X-Ray diffraction of the Al-3Ti-1C master alloy. This figure shows that the master alloy mainly contains three phases, TiC, Ti6C3.75 and TiAl3, embedded in Al matrix.

Microstructure of Al-3Ti-1C master alloy with flake-like TiAl3, TiC and Ti6C3.75 particles in Al matrix is shown in Figure 4. The EDS spectrums of the phases 1, 2 and 3 in the microstructure of master alloy are shown in Figure 5. Figure 4(a) shows that TiAl3, Ti6C3.75 and TiC particles are distributed in Al matrix uniformly. Figure 4(b) shows TiAl3 plates with above 50 µm length are surrounded with lots of sub-micron size TiC and Ti6C3.75 particles which are disconnected. This feature is related to high melting temperature and long holding time [16] . In higher magnification, TiC particles with approximately 2 µm diameters are shown (Figure 4(c)).

Figure 1. TiC powders that added to Al melt as the grain refiner.

Figure 2. Cooling rate of master alloy in the permanent mould.

Figure 3. X-ray diffraction of Al-Ti-C that cooled in preheated permanent mould.

Figure 4. Microstructure of master alloy with different magnification: (a) 100×; (b) 800×; (c) 6400×.

The majority of the fine TiC particles are equiaxed and their surfaces are clear and regular. These have a large effect on grain refining efficiency [17] .

Figure 5(a) shows the analysis of position 1. This position has very low carbon and high titanium; thus it’s TiAl3 phase. Figure 5(b) has more carbon and less titanium; this phase is TiC that is present in position 2. Energy dispersive X-ray analysis spectrum of position 3 is shown in Figure 5(c). This position has high amounts of carbon and titanium and its phase is Ti6C3.75.

Furthermore, distribution of different phases including TiC, TiAl3 and Ti6C3.75 are shown in Figure 6. This figure shows that TiAl3 phase is more than others. Ti6C3.75 is a little more than TiC but sum of both of them is less than TiAl3. This amount of TiAl3 phase improves the fading time of Al-3Ti-1C master alloy.

Figure 5. Energy dispersive X-ray analysis of Al-3Ti-1C master alloy in place: (a) 1; (b) 2; (c) 3 of Figure 5(b).

Figure 6. Distribution of different phases including TiC, TiAl3 and Ti6C3.75.

The macrostructure of commercial pure Al refined with Al-3Ti-1C master alloy is shown in Figure 7. As it can be seen, by increasing the fading time to 15 min, the grain refining efficiency of Al-3Ti-1C master alloy has increased because of coarse shapes of TiAl3 phase. So, TiAl3 phase needs a long time for dissolution. Kori and Zhang [18] [19] reported that the fading time of Al-Ti-C master alloy is 15 min, and Al-3Ti-1C in this work has a same fading time. Fading time in this investigation is because of high temperature in producing master alloy step and coarse TiAl3 particles. This has been previously reported [20] .

A compression between the efficiency of TiC powder and Al-3Ti-1C in grain refining is shown in Figure 8. The grain size was calculated from linear method. A minimum grain size is achieved in about 15 min for both TiC powder and master alloy. Overall, the ability of master alloy in refining is higher than TiC powder.

Figure 7. Macrostructure of aluminum samples, pouring temperature was 720˚C and addition level was 200 ppm of Al-3Ti-1C at different fading times; (a) without grain refiner; (b) 5 min; (c) 15 min; (d) 30 min; (e) 60 min; (f) 120 min.

Figure 8. Variation of grain size with holding time.

4. Conclusions

In Al-Ti-C master alloy, the size, surface characteristic and distribution of carbides and aluminides, as well as the morphology and size of TiC and TiAl3, are related to the melting temperature, holding time, etc.

The Al-Ti-C master alloy, which was manufactured at 1200˚C and 1 hour, holding time, with narrow TiAl3, fine TiC and Ti6C3.75 phases, has a good grain refining efficiency and fading time behavior.

In this type of grain refiner, the optimum time of using is 15 minutes and in more than 60 minutes the grain refining efficiency is not good.

In overall, grain refining of Al-3Ti-1C master alloy is better than TiC powder.


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