3.1. Refinement of the Si Structure in the AC4CH Alloy
The Si grains at various melting times following the addition of Si to virgin Al are presented in
Figure 4. The shorter the melting time of the Si, the greater the number of Si grains that precipitate in the form of primary crystals. The large amount of Si crystals observed might be because they were not degraded until the atom phase due to lack of energy and were precipitated during solidification, though they were melted well [
20]. Therefore, Si crystallization can be minimized by increasing the melting time after the addition of Si during the alloy process. This means that instead of employing simple melting and mixing to form the alloy, the melting time should be long enough for Si to degrade into an atom phase so that a proper AC4CH alloy can form.
Following the addition of Si, P was added to the virgin Al to control the size of the Si grain. The results are presented in
Figure 5. The microstructures of the alloy were compared and analyzed after the addition of Si, while the amount of P was changed 2 h after Si addition. When 30 ppm P was added, Si was formed as the primary crystal. Although P was added because it could not restrict the growth of Si grains, Si precipitated as crystals. The presence of Si grains was attributed to the brittleness of the grain boundary, which caused elongation and a deterioration in the tensile strength. When 40 ppm P was added, Si remained as the primary crystal, and irregular and thick acicular Si crystals were observed. This phenomenon might be because AIP formed incomplete and uneven nuclei, which could not restrict the growth of the Si grain [
21,
22]. However, when 50 ppm P was added, fine Si grains were formed, and the acicular Si crystals were dispersed. Further, when 60 ppm of P was added, grains finer than those in the case with 50 ppm P were formed, and acicular Si crystals were also modified to finer fibers. However, when 70 ppm P was added, the Si grains grew rather irregularly and precipitated, and the acicular Si crystals increased in thickness. Such phenomena might be due to the excessive modification that appeared in the hypereutectic alloy. If the amount of AIP increases excessively, coalescing between AIPs occurs. As a result, AIP loses its function as a nucleus that combines with Si, ultimately leading to the formation of large structures. These results reveal that excellent structures can be obtained when P is in the range of 50–60 ppm, as Si grain growth is restricted under these conditions.
Grain refinement could not be achieved with the addition of only P; therefore, Sr was also added, and the changes in the alloy structure were examined.
Figure 6 shows the Si crystals of the alloy to which varying amounts of Sr were added. Initially, 60 ppm P was added to the virgin Al to reduce the size of the Si grain; afterwards, Sr was added. When 50 ppm Sr was added, the acicular Si crystals remained almost unchanged. Furthermore, when 80 ppm Sr was added, the crystals were not evenly modified, resulting in an Si structure that was not refined, as the acicular Si crystals remained. However, when 120 ppm and 150 ppm Sr were added, although refined Si structures were confirmed in both cases, numerous fine Si crystals precipitated on the dendrite boundary surface. Finally, when more than 180 ppm Sr was added, small modified Si structures were observed. Because molten Al
4Si
2Sr contained a considerable amount of Sr, the Si structure was sufficiently refined, i.e., Si did not precipitate as crystals and was refined on the boundary surface of the crystal, indicating that modification of the structure was successful [
23,
24].
The addition of Sr to molten alloy to form Al
2Si
2Sr resulted in the formation of a refined Si crystal [
25]. However, the Sr that was bound during this reaction might have separated at the top of the molten metal or oxidized to SrO and disappeared naturally. The alloy structure might therefore have changed to a needle-like structure again or growing [
26]. Therefore, changes in the structure owing to the duration of the casting time were observed and used to determine the optimal casting time after addition of Sr.
Figure 7 shows the changes in the alloy structure according to the casting time after the addition of Sr. It was found that the Sr structure was the finest after 10 min following 180 ppm Sr addition, and the refined structure could be maintained for 40 min after Sr addition. However, at 60 min following Sr addition, the fine structure transformed into a needle-like structure. This might be because sufficient Al
2Si
2Sr could not form as the concentration of Sr reduced over time [
27]. Therefore, to maintain the modified Sr structure, the casting duration should not exceed 40 min after the addition of 180 ppm Sr, and if the casting duration exceeds 40 min, additional Sr must be added to the melt so that the excellent alloy structure can be maintained.
3.2. Grain Refinement of the AC4CH Alloy
Various materials were added to reduce the size of the grains to refine the alloy grains. A total of 60 ppm P and 180 ppm Sr were added to the virgin Al, in which only the sizes of Si crystals were controlled to investigate the effect of the added material on the grain size. The resulting crystal sizes were measured, as shown in
Figure 8. While the crystals were not modified, the size of the crystal was as small as 900
m and as large as 1800–2200
m, displaying a very irregular distribution. The larger the grain size, the more inferior the mechanical properties, and there was a possibility of defects due to gas or oxide inclusion between the grains [
28].
Figure 9 shows the results of the addition of the Al-5Ti-1B master alloy, which has been widely used to refine grains. Each of the Al-5Ti-1B master alloys at 0.05%, 0.1%, and 0.2% were added to the molten metal, and the sizes of the grains were compared. When 0.05% Al-5Ti-1B master alloy was added, the size of the grains was in the range of 800–1100
m. However, overall, the grains were not refined and the size of the grains was formed non-uniformly. Into 0.05% Al-5Ti-1B, 25 ppm Ti and 5 ppm B were added. Therefore, the amount of TiAl
3 and AlB
2 that could refine the grains might be lower. In other words, although the size of the grains became smaller with no grain modification, it seems that TiAl
3 and AlB
2 do not solute [
29]. Further, when 0.1% Al-5Ti-1B master alloy was added, the sizes of the grains were in the range of 600–850
m, which was generally large, and their sizes were not uniform. Once again, when 0.2% Al-5Ti-1B master alloy was added, the grain size was in the range of 450–550
m. Even with 25 ppm Ti and 5 ppm B, grain refinement was not well executed. This might not be due to lack of TiAl
3 and AlB
2, but the melting points of precipitated TiAl
3 and AlB
2 were high, consuming more time and energy to be degraded to the atomic state; thus, it is hard to be melted into the Al atoms [
30]. If a larger amount of Al-5Ti-1B master alloy had been employed, the maximum solution amount of Ti would have been in excess, resulting in the precipitation of TiAl
3 and AlB
2 on the boundary surface, which might have impaired its castability.
Figure 10 shows the grains of the AC4CH alloy into which Ti and B were chemically added. With the chemical addition method, the compound was degraded in the molten metal, and Ti and B atoms were produced. These atoms reacted with Al to produce TiAl
3 and AlB
2. K
2TiF
6 at 0.014% and KBF
4 at 0.013% were added to adjust the Ti concentration to 25 ppm and B at 5 ppm. The grain size after the addition of Ti and B was measured as 600–750 μm. Although the size of the grains was large and uneven, the grain refinement was far better than when the Al-5Ti-1B master alloy was added.
In another test, 50 ppm Ti and 10 ppm B were added in the form of 0.028% K
2TiF
6 and 0.025% KBF
4. In this case, the average grain size was 250–450 μm. Therefore, excellently refined grains and slightly large grains were generated. This was because low quantities of TiAl
3 and AlB
2 were produced, causing deviations in the solid solution [
30]. From the above results, it is clear that higher amounts of Ti and B were needed to produce sufficient quantities of TiAl
3 and AlB
2. Therefore, 0.06% K
2TiF
6 and 0.05% KBF
4 were added to adjust the Ti concentration to 100 ppm and B concentration to 20 ppm. The resulting average size of the grains, whose size was controlled and evenly distributed, was 300–400 μm. This might be because, with the Al-5Ti-1B master alloy, the melting points of the TiAl
3 and AlB
2 grains, which were formed in the master alloy, were high; therefore, high energy and time were required to degrade them. However, when Ti and B were added through the K
2TiF
6 and KBF
4 compounds, TiAl
3 and AlB
2, which were bound in the form of atoms, quickly released their Al atoms, forming finer and uniform grains [
31].
To refine the grains, Ti and B, as well as compounds containing C, were chemically added to the AC4CH alloy to form TiAl
3, AlB
2, and TiC.
Figure 11 shows the microscopic images after the addition of Ti, B, and C to the molten metal, and grain size refinement. In addition, 0.0085% K
2TiF
6, 0.013% KBF
4, and 0.002% C
2Cl
6 were added to adjust the concentrations of Ti, B, and C to 15 ppm, 5 ppm, and 1 ppm. The combination of the added materials yielded uniform grains with a grain size of 350–400 μm. Furthermore, 0.033% K
2TiF
6, 0.05% KBF
4, and 0.008% C
2Cl
6 were added to adjust the concentrations of Ti, B, and C to 60 ppm, 20 ppm, and 4 ppm. This combination further improved the grain size to 200–250 μm. Specifically, the Al-5Ti-1B master alloy was added at 0.2% for refinement of the alloy, while when Ti, B, and C were added chemically, the refinement effect was maximized even with far smaller amounts.
3.4. Changes in Mechanical Properties by Heat Treatment Methods
The process was changed at the casting stage to improve the mechanical properties of the AC4CH alloy.
Table 5 and
Table 6 shows the measurement results for mechanical properties such as the tensile strength, yield strength, elongation, hardness, and S-DAS by varying the temperature and time of the solution treatment and aging treatment.
In the 1st alloy, 60 ppm P and 180 ppm Sr were added to control the Sr grain by refinement and granulation. The temperature of the molten metal was maintained at 730 °C, and the mold was heated to 450 °C for alloy preparation. The solution treatments at 535 °C for 8 h and at 155 °C for 6 h were intended to increase the precipitation of Mg
2Si on the aluminum grain boundary surface. The resulting 1st alloys had an excessive amount of Si, and the tensile strength and yield strength were high while the precipitation of Mg
2Si increased during heat treatment [
32]. However, the elongation was low at 8% and hardness did not improve. The grain was not refined as well as the S-DAS, exhibiting small surface areas in the grain, indicating that Mg
2Si might have not gone through a smooth solid solution [
33]. Therefore, precipitation hardening did not contribute to hardening improvement.
For the 2nd alloy, 60 ppm P and 180 ppm Sr were added to virgin Al to reduce the size of the Si grain. Another 60 ppm Ti, 20 ppm B, and 4 ppm C were added to refine the grain to 200–250 μm. During casting, the temperature of the molten metal was maintained at 730 °C, and the mold was preheated to 450 °C for alloy preparation. The heat treatment was executed as a solution treatment at 540 °C for 4 h to expedite formation of the Al-Si-Mg
2Si solution and to raise the degradation speed. Meanwhile, the aging treatment was carried out at 170 °C for 6 h to generate enough of the molten solution, as the alloy would not form a solution properly due to the elution at the surface of the alloy at high temperature. Furthermore, the refinement of the S-DAS was also confirmed when the grain was refined. Although the tensile strength and yield strength decreased as compared to those in the 1st alloy, the hardness was increased by 10/500 (80 HBW), and the elongation was also increased to 10.8%. This might be because hardening of the solution occurred as the amount of solution increased in Mg
2Si during the refinement and aging treatments [
34]. The average S-DAS was 41 μm, which was slightly high, indicating that with grain refinement, the S-DAS could not be granulized, which could be improved through additional refinement of the S-DAS to improve the mechanical properties of the AC4CH alloy.
For the 3rd alloy, 60 ppm P and 180 ppm Sr were added to control the size of the Si grains, and an additional 60 ppm Ti, 20 ppm B, and 4 ppm C were introduced for grain refinement, which resulted in grain sizes of 200–250 μm. Based on the 1st and 2nd alloy results, the amount of Si was slightly reduced to improve the precipitation on the grain boundary surface to increase the elongation by increasing Mg
2Si formation so that the hardness could be improved (
Table 4). Casting was again executed after setting the temperature of the molten metal at 730 °C for fast cooling, and the mold was preheated to 300 °C to prepare the test specimens. The solution treatment duration was increased to 6 h so that Mg
2Si could completely melt, and the aging temperature was reduced to 160 °C to strengthen the hardening of the solution. The casting time was also reduced to 4 h to reduce the time during which precipitation was formed on the grain boundary. The results revealed that, although the tensile strength and yield strength were slightly reduced compared to those in the 2nd test, the elongation remarkably increased to 23%. The hardness might have increased owing to increases in the refinement of the S-DAS and the amount of Mg
2Si formed. In particular, the elongation remarkably increased, which was attributed to the refinement of the S-DAS. Meanwhile, Si precipitation on the grain boundary surface decreased and the dispersed structure could be achieved by the refinement of the Si and Mg
2Si S-DAS, which in turn might have slightly impaired the tensile strength and yield strength [
35].
Despite the remarkable increase in the elongation of the 3rd alloy, the hardness was still low. To further increase the hardness, the solution treatments were again executed at 535 °C and 540 °C for 8 h each, and the aging treatments were performed at 160 °C, 170 °C, and 180 °C for 7 h each. The heat treatments were intended to allow the added elements to become complete solutions, and the changes in the hardness for each temperature were measured.
The hardness test results for different heat treatments are tabulated in
Table 7. The treatments performed for 7 h to promote the degradation of Mg
2Si into a solution and to make the aging treatment sufficiently equilibrated yielded higher hardness values of more than 100 (HBW 10/500). At a solution temperature of 535 °C, the hardness value was high. However, when the solution temperature was increased to 540 °C, the Al-Si-Mg
2Si alloy could not be degraded. Instead coalescence occurred, which might have impaired the hardness. The maximum hardness values were obtained at an aging temperature of 180 °C, which might be because, the higher the aging temperature, the greater the amount of Mg
2Si that degrades, forming a solution that results in a higher hardness. This means that solution treatment should be executed at a temperature that does not encourage the alloy molecules to coalesce with each other. It should be noted that the hardness due to hardening of the solution was higher than that due to precipitation of Mg
2Si.
3.6. Durability Test Results for the Engine
A cylinder block was fabricated using the modified AC4CH alloy chosen in this study, and a durability test for the cylinder block was performed for 300 h. After the durability test, the engine was dismantled for examination.
Figure 14 shows photographs of the cylinder block dismantled after the 300 h durability test. Although the test was executed while driving the cylinder block under harsh conditions, the abrasion of the cylinder block horning was fair, and damage or cracks were not observed. However, at the contact portion between the piston top and the second land, minute polishing occurred, which might be due to carbon precipitated between the piston and cylinder block. Still, there was no sculping due to the polishing or functional problems such as impairment of the compressive pressure. Therefore, if the modified AC4CH material were applied to the cylinder block, the durability of the engine could be secured.
The maximum torques were measured with an engine dynamometer during the durability test, and the fuel consumption was also measured using a flowmeter. The relationship between the torque and output is given by Equation (5). The fuel consumption of the engine can be expressed as a break-specific fuel consumption (BSFC), which is the fuel consumption rate per unit output, and can be calculated by using Equation (6). The changes in the engine torque and BSFC measured during the 300 h durability test are presented in
Figure 15 and
Figure 16. As the durability test progressed, the engine stabilized as the mechanical aging progressed, while decrements in the torque and BSFC gradually diminished. Specifically, the boost-up by the turbocharger started in full swing, and from 1500 rpm, when the combustion stabilized, the differences between the starting and final values of both the torque and BSFC were within 5%. Therefore, when the modified AC4CH material was used for the cylinder block, the durability of the engine cylinder black could be secured.
where:
: Engine power (kW); N: Engine rotational speed (rev/s); T: Engine torque (Nm);
: mass flow of fuel (g/h).