Research Article | Open Access
Wanwu Ding, Wenjun Zhao, Tiandong Xia, "A Precipitation Phenomenon of Titanium Compounds in Aluminum Melts and the Refinement Fading Mechanism of the Al-5Ti-0.62C Master Alloy", Advances in Materials Science and Engineering, vol. 2015, Article ID 430156, 9 pages, 2015. https://doi.org/10.1155/2015/430156
A Precipitation Phenomenon of Titanium Compounds in Aluminum Melts and the Refinement Fading Mechanism of the Al-5Ti-0.62C Master Alloy
The Al-5Ti-0.62C master alloy was prepared through a method of thermal explosion in molten aluminum. The process of remelting and refining of commercially pure aluminum was conducted, and precipitation samples with different heat-treatment times were obtained. Scanning electron microscopy (SEM), X-ray diffraction (XRD), optical microscopy (OM), and other techniques were used to analyze the microstructure of the precipitates at the bottom of the samples so as to explore the fading mechanism of Al-Ti-C alloy refinement. The results showed that an obvious precipitation phenomenon of titanium compounds existed in the remelted Al-5Ti-0.62C master alloy and that there were both TiC compounds and TiAl3 compounds in the precipitates; in the refined pure aluminum samples, the precipitates were mainly TiC compounds. Precipitation of titanium compounds in aluminum melting is the main cause of fading in the refinement effect of an Al-Ti-C master alloy.
With their good grain refining effect, aluminum alloy grain refiners are widely used during the process of melting and casting of aluminum and its alloys . Currently, the most frequently used are grain refiners of the Al-Ti-B series . However, during their use, it is found that TiB2 particles are easily aggregated and precipitated and even show a so-called poisoning phenomenon of grain refiners in the melting and casting process, severely reducing the grain refinement effect of grain refiners and resulting in coarse grains that will affect the subsequent related performances of the casting ingots [3–5]. In recent years, Al-Ti-C grain refiners have received increasing attention. Studies have shown that in some cases , Al-Ti-C exhibits a better refining effect than Al-Ti-B does, and the wide variety of sources of C can help achieve greener production . The Al-Ti-C master alloy is considered to be a grain refiner that has good applicability and is the most studied [8–11]. The relationships among preparative technology, microstructure of the Al-Ti-C master alloy, and its refining effect, as well as their collective refinement and poisoning mechanisms, have been studied both at home and abroad [12–14]. As investigators continue to deepen their understanding of the grain refinement phenomenon, they have proposed many theories  aimed at grain refinement mechanisms, but there have been to the present time no unified views offered. Grain refinement mechanisms of aluminum and aluminum alloys are very complex, so it is still very difficult to fully resolve their refinement processes and mechanisms. In the present study we aimed to conduct an in-depth analysis of mechanisms of refinement fading of the Al-Ti-C alloy through the analysis of the precipitation phenomenon in the remelting process of the Al-5Ti-0.62C master alloy and the process of refining of commercially pure aluminum; this will provide clarification of the preparation and application and refinement of the fading mechanism of Al-Ti-C alloys.
2. Experimental Materials and Methods
The primary materials used in the experiments included Al powder (99.6%), Ti powder (99.3%), C powder (99.8%), and commercially pure aluminum. The supplier, particle size of the powders, and purity are given in Table 1. The main raw materials were made through ball mixing and cold pressing into prefabricated blocks. The molar ratio of the composition of prefabricated blocks containing Al, Ti, and C powders was 5 : 2 : 1. The prefabricated blocks went through a thermal explosion reaction in pure molten aluminum at a temperature of 780°C [16, 17].
The same quality Al-5Ti-0.62C master alloy was placed in an Al2O3 crucible for heating and melting. At a temperature of 730°C, the Al-5Ti-0.62C alloy melted and was preserved for 30 min, 60 min, 120 min, or 180 min before each was naturally cooled in the crucible. The grain refinement experiment was carried out in a well-type resistance furnace. A certain amount of commercially pure aluminum was melted in an Al2O3 crucible and when the temperature of the aluminum melt rose to °C, and, after refining, stirring, and skimming, we added the Al-5Ti-0.62C master alloy with a mass fraction of 0.4%. After the Al-5Ti-0.62C master alloy was added into the aluminum melt, it was sufficiently stirred so as to allow it to melt and mix well. It was held for 20 or 120 min, before it was naturally cooled in the crucible. In order to investigate the role of melt agitation on precipitation, the refined sample which was made through the above methods and preserved for 120 min was sufficiently stirred before being allowed to cool naturally.
The cooled and solidified sample was removed from the crucible, and the ingot was sawed longitudinally exactly in the center. All of the samples were sand papered, polished, and etched with a reagent (60% HCl + 30% HNO3 + 5% HF + 5% H2O, volume fractions). Finally, the analysis was conducted on the phase composition, microstructure morphology, and components of the alloy with a RigakuD/max-A X-ray diffraction meter (XRD, PW 3040/60, PANalytical, Rotterdam, Holland), large optical microscope (OM, MEF3, Leica Inc, Austria), and a JSM-7500 scanning electron microscope (SEM, SSX-550 fitted with EDS equipment, Shimadzu Corporation, Kyoto, Japan).
3. Results and Discussion
3.1. Microstructures of Al-5Ti-0.62C Alloys
Figure 1 shows the XRD (X-ray diffraction) pattern of the Al-5Ti-0.62C alloys. The Al-5Ti-0.62C alloy is composed of Al, TiAl3, and TiC. Figure 2(a) shows the OM photograph of the Al-5Ti-0.62C alloy. We observed on the Al substrate of the Al-5Ti-0.62C alloy a large number of strip-like or lump-like substances that were uniformly distributed with a size of roughly 20–55 μm in length and 8–12 μm in width, as well as small black particles. Figures 2(b) and 2(c) show the SEM image of the strip-like substances and that of the small black particles. Table 2 shows the analysis results of the energy spectrum of the chemical composition of point A in lump-like substances and of point B in small particles in Figure 2. From Table 2, we can see that at point A in the strip-like substances, the molar mass fraction of elemental Al was 69.72%, the molar mass fraction of elemental Ti was 21.85%, and the molar mass ratio between elemental Al and elemental Ti was 3.19. At point B in the small particles, the molar mass fraction of elemental C was 27.98%, the molar mass fraction of elemental Ti was 25.52%, and the molar mass ratio between elemental C and elemental Ti was 1.1. According to the analysis results from the XRD pattern of the Al-5Ti-0.62C alloy, we could see that the strip-like substances in Figure 2(b) were TiAl3, and the small black particles in Figure 2(c) were TiC. From the above analysis, we knew that in the Al-5Ti-0.62C alloys used in the experiment a large number of strip-like or lump-like TiAl3 and TiC particles were found and distributed in a dispersed and uniform manner.
3.2. Study of the Precipitation Phenomenon of the Titanium Compound
Figure 3 shows the macrographs of the longitudinal section of the samples obtained after remelting the Al-5Ti-0.62C master alloy over different heat-treatment periods. As can be seen from Figure 3, after different heat-treatment periods of remelting, an apparent stratification phenomenon was observed in all of the macroscopic samples. Figure 4 shows the microstructure of the remelted Al-5Ti-0.62C master alloy with a heat-treatment time of 180 min. As can be seen from Figure 4(a), after remelting and heat preservation for 180 min, the microstructure of the top portion of the sample shown in Figure 3(d) shows almost no particles. However, a severe segregation phenomenon appeared at the stratification portion (Figure 4(b)), and there appeared at the lower portion of the stratification a large number of sediment layers primarily composed of aggregated particles and strip-like or lump-like substances (Figure 4(c)). Table 3 depicts the EDS results of the chemical compositions of point A of strip-like substances in the deposited layer and of point B of black aggregated particles at the grain boundary. Table 3 illustrates that at point A of the strip-like substances, the molar mass fraction of elemental Al was 77.38%, the molar mass fraction of elemental Ti was 22.62%, and the molar mass ratio between elemental Al and elemental Ti was 3.4, while, at point B of the aggregated particles, the molar mass fraction of elemental C was 25.29%, the molar mass fraction of elemental Ti was 22.31%, and the molar mass ratio between elemental C and elemental Ti was 1.1; this confirmed that the strip-like substances in the precipitation layer were TiAl3, and the aggregated particles were TiC. Figure 5 depicts the microstructures of the precipitation layers at the bottom of the samples of the remelted Al-5Ti-0.62C master alloy after different heat-treatment times. As can be seen, after different times of remelting the Al-5Ti-0.62C master alloy, the precipitates at the bottom of the samples were still mainly aggregated particles and strip-like or lump-like substances. According to the SEM image (Figure 6) and EDS results of the chemical compositions of the black aggregated particles at the grain boundary (Table 4) and the precipitation layers at the bottom of the sample of the remelted Al-5Ti-0.62C master alloy after a heat-treatment time of 180 min, we observed that precipitates at the bottom of the sample were still TiAl3 and TiC.
Figure 7 shows the precipitates at the bottom of the samples after different heat-treatment times during the refinement of commercially pure aluminum by the Al-5Ti-0.62C master alloy. It can be seen from Figure 7(a) that after a heat-treatment time of 20 min, there was a small amount of precipitate at the bottom of the sample; but when the heat-treatment time was 120 min, a large amount of precipitate appeared at the bottom of the sample. As can be seen from the mapping analysis results of the precipitates at the bottom of the samples refined with the Al-5Ti-0.62C master alloy after 120 min of heat treatment (Figure 8), the particles that aggregated at the grain boundary were rich in the elements Ti and C. Figure 9 shows the line scanning and EDS spectrum of aggregates at the grain boundary of α-Al in Figure 8(a). According to the line scanning (Figure 9(a)) and point analysis (Figure 9(b)) results of the particles at the grain boundary, we can observe that the precipitates at the bottom of the sample in Figure 8(a) were mainly the TiC particles added to the Al-5Ti-0.62C master alloy; that is, TiC precipitation occurred. Small lump-like or strip-like TiAl3 were not found to exist in the precipitates of the refinement sample, which was due to the fact that in the case of less added alloy; the TiAl3 added to the aluminum melt was melted in a short period of time before it precipitated to the bottom of the sample and became the Ti solute  in the aluminum melt.
3.3. Discussion of the Refinement Fading Mechanism of the Al-5Ti-0.62C Alloy
From the above analysis, we observed that the Al-5Ti-0.62C master alloy melt severely segregated during the process of heat treatment and that this segregation was caused by the sinking of TiAl3 and TiC in liquid aluminum as affected by gravity. Dissolution occurred when TiAl3 was in the molten aluminum for a long period of time and preferential growth occurred during the solidification process after complete dissolution; that is, the vertical growth rate of the plane whose crystal atoms of the body-centered cube were arranged most loosely was the fastest, while the growth rate of the closely packed plane was the slowest . During the sinking process, because of the poor wettability between TiC particles and the aluminum melt, there existed a very high interfacial energy at the boundary between TiC particles and liquid aluminum. Excluded by the liquid aluminum, TiC particles aggregated, such that in some areas there was a high density of TiC particles that may even have adhered to one another. According to Stokes’ formula , the sinking speed in the melt particles whose radius is smaller than 0.1 cm is calculated by the following formula: , where is the descending speed of the particles, is the radius of the particles, ρ1 is the density of the particles, ρ2 is the density of the aluminum liquid, and μ is the viscosity of the molten aluminum. It can be seen that the sinking speed of the particles mainly depends on the volume of the particles, the difference between the density of the particles and that of the molten aluminum, and the viscosity of the aluminum fluid. Therefore, when the TiC particles gather into larger particle clusters, the precipitation of TiC will be further accelerated. Due to the structural heredity of the Al-Ti-C master alloy , the precipitation phenomena possess aspects in the refinement process similar to those of the remelting process, such that both TiAl3 and TiC particles introduced during the refinement process aggregate and precipitate, and they only differ in their length of time. When a very small amount of Al-5Ti-0.62C master alloy is added into the molten aluminum, most TiAl3 will dissolve into the molten aluminum and release Ti atoms in the process of sinking. As Ti manifests poor activity between TiC and the aluminum melt , these Ti atoms segregate around the TiC particles, forming the “Ti-rich zone on the TiC/α-Al interface” [18, 22], and become the heterogeneous nucleation core of α (A1) when the aluminum melt solidifies. With the extension of the heat-treatment time for the aluminum melt, a large number of TiC particles deposit at the bottom of the sample; this allows during solidification of the melt only a small amount of residual TiC in the middle and upper portion of the sample to form the “Ti-rich zone on the TiC/α-Al interface” and become nucleation particles. This then causes the phenomenon of refinement fading.
In order to study the role of melt mixing in the process of grain refinement and its effects on TiC precipitation, we allowed sufficient stirring before the natural cooling of the refinement sample after a heat treatment of 120 min. As can be seen from Figure 10, there were almost no precipitates at the bottom of the refinement sample, which had been stirred sufficiently and heat preserved for 120 min. Figure 11 shows the macrographs obtained without stirring and with sufficient stirring before the cooling of the refinement samples after heat treatment of 120 min. As can be seen from Figure 11, significant differences in the grain size exist between the top and bottom of the unstirred sample: the grains at the top of the sample are large, while those at the bottom are small, and the closer to the bottom, the smaller the grains (Figure 11(a)). The difference in grain size between the top and bottom of the sample after sufficient stirring prior to natural cooling was significantly reduced, with the grain size becoming substantially uniform (Figure 11(b)). This shows that stirring action can make parts of the TiC particles redistribute in a dispersed way so as to restore the refinement effect.
(i)The Al-5Ti-0.62C master alloy exhibits an obvious precipitation phenomenon of titanium compounds in the aluminum melt. In the precipitates of the remelted Al-5Ti-0.62C master alloy, there were both TiC compounds and TiAl3 compounds; in the refinement sample of commercially pure aluminum, the precipitates were mainly TiC compounds.(ii)The precipitation of titanium compounds in the aluminum melt is the main cause of the decline in the refinement effect of the Al-5Ti-0.62C master alloy, and sufficient stirring of the melt can thus allow TiC particles to redistribute in a dispersed way so as to restore the refinement effect.
Conflict of Interests
The authors declare that they have no conflict of interests.
This research was financially supported by the National Natural Science Foundation of China (no. 50965012). The authors would like to acknowledge the financial support of the Natural Science Foundation of Gansu Province in China (Grants nos. 1308RJYA088, 1308RJZA291, and 145RJYA295).
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