Effect of cooling slope and manganese on the microstructure of hypereutectic Al-Si alloy with 2 %Fe

Effect of cooling slope and manganese on the microstructure of hypereutectic Al-Si alloy with 2 %Fe

Lu Li^I; Rongfeng Zhou^I,II,*; Dehong Lu^I; Yehua Jiang^I; Rong Zhou^I

^ICollege of Materials Science and Engineering, Kunming University of Science and Technology-KUST, 650039, Kunming, Yunnan, China

^IIResearch Center for Analysis and Measurement, Kunming University of Science and Technology-KUST, 650039, Kunming, Yunnan, China

ABSTRACT

The effect of cooling slope (CS) on the microstructure of hypereutectic Al-22Si-2Fe (% w/w) alloys with 0%, 0.99%, and 1.36% Mn were studied. The results showed that primary Si particles (PSPs), needle-like Fe phases, coarse fishbone-shaped α-Al₁₅(Fe, Mn)₃Si₂ phases, and eutectic Si could be refined. With such a CS process, the intermetallic compounds in the alloys with different Mn/Fe ratios were examined with an optical microscope, scanning electron microscope, and X-ray diffraction. Moreover, the acicular δ-Al₄(Fe, Mn)Si₂ and blocky α-Al₁₅(Fe, Mn)₃Si₂ phases were analyzed by transmission electron microscopy.

Keywords: hypereutectic Al-Si alloys, cooling slope, Mn/Fe ratio, intermetallic compounds

1. Introduction

Hypereutectic Al-Si alloys have low thermal expansion coefficients, excellent wear resistance, and high hardness. Thus, they have been widely used to make wear resistant components in the automotive industry. However, their low toughness and poor ductility, which are caused by harmful morphologies of primary Si particles (PSPs), such as coarse polygonal, star-like, and other irregular shapes, limit the wider application of these alloys. The addition of phosphorous or phosphorous compound to the melt can promote nucleation of PSPs for refining PSPs that can obtain AlP particles¹. However, the refining effect of phosphorous or phosphorous compound on PSPs is limited due to the agglomeration of AIP particles². According to the experiment of predecessors, the equivalent diameter of PSPs modified by phosphorous is not less than 40 µm^[3]. In recent years, the semi-solid processing of hypereutectic Al-Si alloys has been investigated widely. Research shows that PSPs can be refined and their morphology improved by preparing hypereutectic Al-Si alloys semi-solid slurries using cooling slope (CS) casting^4,5.

To replace cast iron with hypereutectic Al-Si alloys, the hypereutectic Al-Si alloys must still have the originally desired mechanical properties. The addition of Fe to the hypereutectic Al-Si alloys can form Fe inter-metallic compounds, which can improve thermal stability. In contrast, Fe compounds such as α-Al₄FeSi₂ and β-Al₅FeSi phases present as acicular structures which result in inferior tensile strength⁶. Some researchers have proved that the morphologies of intermetallic compounds could be modified and presented acicular, Chinese-script shape, fishbone shaped, and block-like respectively with varying contents of Mn is added to the cast Al-Si-Fe alloys under conventional casting condition^7-9. According to the literatures, PSPs and coarse Fe-rich phases also could be refined by spray deposition or ultrasonic vibration process^10-12. Comparing these methods, the cooling process has shorter process flow and lower operating cost. However, systemic researches on the influence and mechanism of Mn addition to the solidification microstructure of such alloys by CS casting have not been reported.

The present study aimed to investigate the effect of segmented cooling plates on the microstructure of hypereutectic Al-22Si-2Fe (% w/w) alloys with 0%, 0.99%, and 1.36% Mn. The effect of Mn/Fe on the CS-cast microstructure of hypereutectic Al-Si alloys was also examined. In addition, the transformations of Fe-rich phases during CS casting process in hypereutectic Al-Si alloys were also discussed.

2. Experimental Work

Hypereutectic Al-22Si-xFe-yMn alloys were prepared from pure Al, Si-7% Fe master alloy, and 75% Mn agent in a 6.5 kW resistance furnace. The process was as follows: pure Al was heated to 850 ºC, blocky Si-7%Fe master alloy at a grain size of 1 to 2 cm diameter wrapped in aluminium foil was rapidly immersed into the molten aluminium in batches and stirred once every twenty minutes until the master alloy had completely melted. Afterwards, the Mn agent with 75% Mn was crushed to a particle diameter of between 1 and 2 cm in diameter before its addition to the molten Al-22Si-xFe alloy. Once the Mn agent had melted, the melt was stirred and insulated for 30 minutes. In the following, phosphorus wrapped with aluminium foils was pressed into the metal and stirred. After being held for 20 minutes, C₂Cl₆ was added for degassing, then the slag was skimmed off. The solidus and liquidus of the three alloys neared 575 and 780 ºC, respectively. Hence, after being held for a further 10 minutes, the melt was cooled to 800 ºC and poured into a high purity graphite crucible 0.06 m in diameter and 0.2 m deep at room temperature by CS technology. CS casting was employed using segmented cooling plates (Figure 1). The chemical composition of the Al-22Si-xFe-yMn alloys studied is listed in Table 1. Due to the material sticking to the surface of traditional integral cooling plates after CS casting, the integral plate was replaced with segmented plates. The lower segmented plate was made of graphite because of the poor wettability between graphite and molten aluminium. Solidified shell layers barely formed on the surface of two plates even though molten alloy flowed through the lower graphite plate after passing through the upper plate. CS casting was carried out in a sealed steel box. Argon at 99.9% purity was pumped in to prevent oxidation during processing. According to previous experiments, fine, regular shaped PSPs could be obtained when the upper steel plate was 30º and the lower graphite plate was 50º, besides, the effective length required of each plate was 0.3 m.

After cooling to room temperature, the melt in the high purity graphite crucible was removed and cut into cylindrical slugs of 0.02 m in diameter and 0.03 m height. The CS casting microstructures of the samples were revealed by etching with 0.5% hydrofluoric acid. The polished and etched specimens were examined with an optical microscope (Leico), scanning electron microscope (SEM), energy spectrum (EDS) analysis system (XL30ESEM-TMP, Philips Co.), and X-ray diffraction (XRD) (D/max-3B, Ricoh Co.), while the solidus and liquidus were evaluated using a simultaneous thermal analyser (NETZSCH STA 499F3). The TEM analysis of Fe-rich phases was carried out using a Tecnai G2 F30 S-TWIN transmission microscopy operated at an acceleration voltage of 300 kV.

3. Results and Discussion

3.1. The influence of segmented cooling plates on alloy morphology

Figure 2 shows the as-cast and CS microstructures of A0, A1, and A2 alloys. The as-cast microstructures of A0, A1, and A2 alloys are shown in Figures 2a, c, and e, respectively. The CS cast microstructures of A0, A1, and A2 alloys are shown in Figures 2b, d, and f. As shown in Figure 2a, the as-cast microstructure of A0 alloy comprises of grey PSPs, white α-Al, a black acicular microstructure, and lamellar eutectic Si. Almost all the α-Al phases are formed around PSPs (45 ± 10 µm equivalent spherical diameter). PSPs exhibit different morphologies such as coarser polygons, and other irregular shapes. It can be seen that the black acicular microstructure in Figure 2a is Fe intermetallic compounds at 100 µm in length. Lamellar eutectic Si phases are uniform distributed in the microstructure. Figure 2b shows CS cast microstructure of A0 alloy, compared with the PSPs in Figure 2a, the equivalent diameter of PSPs that present as block-like is reduced (30 ± 10 µm), and the number of PSPs per unit area is increased in Figure 2b. In addition, the number of black acicular Fe phases also is increased, and the length of Fe phases is reduced to 70 µm. It is worth mentioning that eutectic Si was refined by cooling slope process to present a fibrous morphology. The as-cast microstructure of A1 alloy is shown in Figure 2c, the equivalent diameter of PSPs is 50 ± 10 µm. Compared with Figure 2a, the number of black needle-like Fe intermetallic compounds has been decreased, and their length is reduced to 70 µm. With Mn addition to the alloy, dark grey fishbone-like and block-like Fe-bearing compounds appear in the microstructure. The length of the entire fishbone-like Fe-bearing compound was measured at 200 µm, with a width of 40 µm. PSPs and needle-like Fe intermetallic compounds in the CS cast microstructure of A1 alloy were refined to a certain extent. The dark grey block-like compounds that surround PSPs, instead of coarser fishbone-like structures, appear in the CS cast microstructure of A1 alloy (at an Mn/Fe ratio of 0.52). Figures 2e and f show the as-cast and CS-cast microstructures of A2 alloy, respectively. Comparing two casting methods, the equivalent diameter of PSPs is reduced to 30 µm, and the refinement induced by this CS casting method is apparent. When the Mn/Fe ratio is increased to 0.7 (A2 alloy), there are no acicular Fe intermetallic compounds in the CS-cast microstructure: they are present in the as-cast microstructure. The dark grey compounds are dendritic and irregular in the as-cast. Whereas the dark grey compounds are regular and polygonal in solidification microstructure after the CS process.

 

Under the effect of gravity, the dynamic solidification process of the liquid melt occurred on the surfaces of the cooling plates when the liquid melt flowed through the surfaces of the cooling plates. The growth of PSP was anisotropic due to the Si atoms' greater diffusion. Only under conditions of rapid solidification and high undercooling to increase the nucleation rate, could the preferred orientation growth be inhibited whilst refining the microstructure. Thanks to the strong cooling action of the cooling slope plates, the PSPs' diameter by CS casting decreased relative to that obtained by conventional casting. By CS casting, coarser fishbone-shaped intermetallic compounds were developed in the shape of regular polygons or granules due to the shear force between the cooling plates and the melt and the homogenization of the molten solute. Therefore, intermetallic compounds were formed the blocky structure of Figures 2d and f under the effect of the cooling plates. Umezawa et al.¹³ indicated that hypereutectic Al-18Si alloy with an Mn/Fe ratio of 0.84 under the effect of sloped cooling plates, formed fishbone-shaped intermetallic compounds which could be improved to form blocky structures in the final solidification microstructure.

3.2. The influence of Mn/Fe ratio on the CS-cast microstructure of hypereutectic Al-Si-xFe-yMn alloy

Figure 3a implies that the A0 alloy contains phases of α-Al, PSP, δ-Al₄FeSi₂, and β-Al₅FeSi. As shown in Figure 3b, the equivalent diameter of PSPs is between 30 and 40 µm, acicular Fe phases with length of 100 µm. The α-Al phases are distributed between the microstructures of PSPs and eutectic Si. According to EDS analysis of the acicular intermetallic compound and the composition thereof, its molecular formula was inferred to be Al_3.80FeSi_2.47, which is close to that of the δ-Al₄FeSi₂ phase. Based on related studies¹⁴, metastable δ-Al₄FeSi₂ phase can be transformed to stable β-Al₅FeSi through a peritectic reaction at a low cooling rate. However, this reaction was restricted by the high cooling rate of cooling plates and high purity graphite crucible. Therefore, long acicular intermetallic compounds mainly comprise of δ-Al₄FeSi₂ phases in CS casting A0 alloy.

Figure 4 shows the influence of increasing Mn/Fe ratio on the CS-cast microstructures of Al-22Si-xFe-yMn alloys. Figure 4a shows a BSE micrograph of CS-cast A1 alloy (Mn/Fe = 0.52): acicular Fe phases at a length of about 100 µm are present in the microstructure, bright white compounds attach to PSPs show block-like, or irregular shapes. As the Mn/Fe ratio increased to 0.70, black particulate phases are PSPs with equivalent diameters of about 30 µm, while bright white polygon-shaped compounds at an equivalent diameter of 80 µm attach to the PSPs. Besides, a large number of fine Chinese script-shaped or fishbone-shaped intermetallic compounds evenly distributed could be observed in the eutectic CS-cast microstructures of A2 alloy.

The CS casting alloys A1 and A2, with different Mn/Fe ratios, were investigated by XRD. As shown in Figure 5, the results indicate that a number of different phases were identified unambiguously in the two samples. There are diffraction waves for β-Al₅(Fe, Mn)Si, δ-Al₄(Fe, Mn)Si₂ and α-Al₁₅(Fe, Mn)₃Si₂ as shown in the XRD spectrum for CS-cast A1 alloy. Compared to the XRD spectra for CS-cast A1 alloy, there is no clear diffraction wave for the β-Al₅(Fe, Mn)Si phase as shown for the CS-cast A2 alloy. Only a diffraction wave for the δ-Al₄(Fe, Mn)Si₂ phase could be found implying that a small amount of δ-Al₄(Fe, Mn)Si₂ phase remained in CS-cast A2 alloy albeit at a low concentration.

Figure 6a shows the acicular intermetallic compounds (labelled "A") in A1 alloy, polygon-shaped intermetallic compounds that are formed around to PSP (labelled "B") that can be observed in A2 alloy (shown in Figure 6b). The fine Chinese script-, or fishbone-shaped compounds (labelled "C") can be seen in the microstructure of A2 alloy (shown in Figure 6b). The energy spectrum results for the three compounds above are listed in Table 2. The results show that the compositions of the polygonal blocky compounds and Chinese script-shaped compounds are Al_12.63(Fe, Mn)₃Si_2.33 and Al_16.65(Fe, Mn)₃Si_1.85 respectively, which are similar to the Al₁₅(Fe, Mn)₃Si₂ phase. While the acicular Fe phase's composition in the A1 alloy's microstructure is Al_3.55(Fe, Mn)Si_2.57, which is akin to the δ-Al₄(Fe, Mn)Si₂ phase.

3.3. TEM analysis for the Fe-rich phases in A2 alloy

Figure 7 shows the TEM micrographs and their corresponding selected area diffraction patterns (SADPs) of A1 and A2 alloys. The bright-field TEM image of δ-Al₄(Fe, Mn)Si₂ phase in A1 alloy, and the SADPs pattern taken from the phase are shown in Figure 7a. The SADP corresponds to tetragonal structure, which is the same as the lattice structure of δ-Al₄FeSi₂ phase. According to these results, Mn can substitute Fe in the δ-Al₄FeSi₂ lattice. The blocky Al₁₅(Fe, Mn)₃Si₂ phase (the phase was stroked because the high voltage) and its SADP are shown in Figure 7b. Through the analysis of the SADP, Al₁₅(Fe, Mn)₃Si₂ phases are identified with body centre cubic.

3.4. The transformations of Fe-rich phases during CS casting process

According to the Al-Si-Fe ternary phase diagram¹⁵, the equilibrium solidification of high Si alloys with 2% Fe starts with the formation of a primary Si phase followed by the formation of a δ-Al₄FeSi₂ phase. The primary δ-Al₄FeSi₂ phase can be transformed to stable β-Al₅FeSi phase by a peritectic reaction at lower cooling rates and below 610 ºC. The addition of Mn to the solidification process - without reaction but with just replacement of atoms due to a low Mn content - lead to the coexistence of Fe and Mn atoms in the lattice of the δ phase¹⁶. Therefore, the equilibrium solidification of high Si alloys with Mn/Fe ratios of 0.52 started with a primary Si phase. As the solidification proceeded, the δ-Al₄(Fe, Mn)Si₂ phase crystallised. Research by Huang et al.¹⁰ suggested that crystallised δ-Al₄(Fe, Mn)Si₂ phases react with the liquid phase to produce an α-Al₁₅(Fe, Mn)₃Si₂ phase. Moreover, δ-Al₄(Fe, Mn)Si₂ phases are involved in the peritectic reaction causing transformation to acicular β-Al₅(Fe, Mn)Si phases below 610 ºC. The remaining liquid phase is then solidified at its eutectic temperature, and a eutectic Si, α-Al and Chinese script-, or fishbone-shaped α-Al₁₅(Fe, Mn)₃Si₂ were precipitated in the quaternary eutectic reaction.

Hypereutectic Al-22Si with an Mn/Fe ratio of 0.52 (A1 alloy), under the action of the cooling plates, entailed the crystallisation of a large amount of PSPs, followed by the formation of a δ-Al₄(Fe, Mn)Si₂ phase. However, the strong cooling effect inhibited the transformation of metastable δ-Al₄(Fe, Mn)Si₂ to α-Al₁₅(Fe, Mn)₃Si₂ while the δ-Al₄(Fe, Mn)Si₂ that does not participate in the conversion was transformed to stable β-Al₅(Fe, Mn)Si at temperatures below 610 ºC. The author measured the temperature at which the melt flowed out of cooling plates at 650 ºC, and the conversion from δ-Al₄(Fe, Mn)Si₂ to β-Al₅(Fe, Mn)Si below 610 ºC occurred at room temperature in the high purity graphite crucible. Since the melt's cooling rate was accelerated due to the high thermal conductivity of the graphite crucible, the conversion of δ-Al₄(Fe, Mn)Si₂ to β-Al₅(Fe, Mn)Si cannot be completed, and some of the δ-Al₄(Fe, Mn)Si₂ phase remained in the solidified microstructure. Therefore, the diffraction peaks of the three compounds can all be observed in the XRD spectra of CS-cast A1 alloy samples (Figure 5a). Then the remaining liquid phase solidified at its eutectic temperature, and Chinese script-shaped or fishbone-shaped α-Al₁₅(Fe, Mn)₃Si₂ would then have been crystallised in a quaternary eutectic reaction. In reality, few eutectic α-Al₁₅(Fe, Mn)₃Si₂ phases formed below the eutectic temperature because the Mn content added to the alloy was low.

When the Mn/Fe ratio was 0.70, acicular Fe phases cannot be observed in the microstructure of A2 alloy (see Figures 4b and 6b). Research by Huang et al.¹⁰ proved that phases of PSP, α-Al, β-Al₅(Fe, Mn)Si, δ-Al₄(Fe, Mn)Si₂, and α-Al₁₅(Fe, Mn)₃Si₂ coexisted in the alloy in the solidification of hypereutectic Al-Si with added Mn and Fe elements such that Mn/Fe = 0.625. Meanwhile, they pointed out that only an α-Al₁₅(Fe, Mn)₃Si₂ phase, as an intermetallic compound, was present at Mn/Fe = 1. In addition, some researchers noted¹¹ that, the formation of α-Al₁₅(Fe, Mn)₃Si₂ can be promoted by adding Mn: with increasing Mn content, the crystallisation temperature range of δ-Al₄(Fe, Mn)Si₂ is narrowed, and the crystallisation temperature range of α-Al₁₅(Fe, Mn)₃Si₂ is broadened. The α-Al₁₅(Fe, Mn)₃Si₂ phase may be primary since plenty Mn and Fe were added to high Si alloys¹⁷.

During the CS casting process of A2 alloy at Mn/Fe = 0.7, PSPs and a small amount of δ-Al₄(Fe, Mn)Si₂, firstly crystallised at higher temperatures: then a large amount of α-Al₁₅(Fe, Mn)₃Si₂ formed and the residual δ-Al₄(Fe, Mn)Si₂ was transformed to β-Al₅(Fe, Mn)Si at below 610 ºC. Although the diffraction peak of the acicular δ-Al₄(Fe, Mn)Si₂ phase can be found in A2 alloy, it proved difficult to find in the microstructure due to its reduced nucleation site activity in the initial solidification stage. Moreover, δ-Al₄(Fe, Mn)Si₂ phases were involved in the peritectic reaction forming the acicular β-Al₅(Fe, Mn)Si phase below 610 ºC. Owing to the low amount of δ-Al₄(Fe, Mn)Si₂ in the reaction, nearly no β-Al₅(Fe, Mn)Si phases were induced. Then the remaining liquid phase solidified at its eutectic temperature, and many Chinese script-, or fishbone-shaped α-Al₁₅(Fe, Mn)₃Si₂ particles were precipitated in the ensuing quaternary eutectic reaction. Based on the above reasoning, it was concluded that at Mn/Fe = 0.70, there were no obvious acicular Fe phases discernible, and the intermetallic compounds mainly comprised blocky and Chinese script-, or fishbone-shaped α-Al₁₅(Fe, Mn)₃Si₂ phases in the microstructure.

4. Conclusions

• The slope angle of the upper steel plate is 30º, while that of the lower graphite plate is 50º. Besides, the effective length required of each plate is 0.3 m, fine, regular-shaped PSPs can be obtained. In addition, acicular Fe phases, coarser fishbone-shaped α-Al₁₅(Fe, Mn)₃Si₂ phases, and eutectic Si can be refined by the CS process;

• The as-cast microstructure of the A0 alloy comprises grey PSPs 50 µm in equivalent diameter, white α-Al, black acicular Fe phases 100 µm in length, and lamellar eutectic Si. Without CS processing, acicular δ-Al₄(Fe, Mn)Si₂ phase, β-Al₅(Fe, Mn)Si phase, and coarser fishbone-shaped α-Al₁₅(Fe, Mn)₃Si₂ phase coexist in the solidification microstructure of the alloy with an Mn/Fe ratio 0.52. Without CS-processing, acicular Fe phases can be observed and only coarser fishbone-shaped and fine α-Al₁₅(Fe, Mn)₃Si₂ phases are seen in the microstructure of the alloy with 1.35 % Mn content;

• Through the analysis of the SADPs, the lattice structures of acicular δ-Al₄(Fe, Mn)Si₂ and α-Al₁₅(Fe, Mn)₃Si₂ phases are identified with tetragonal structure and body centre cubic, respectively;

• As Mn/Fe ratio is 0, acicular δ-Al₄FeSi₂ phases, as a main intermetallic compound, are present in the CS-cast microstructure of the A0 alloy. With CS-processing, the alloy with an Mn/Fe ratio of 0.52 has the δ-Al₄(Fe, Mn)Si₂ phases as its main acicular Fe-rich phase, and the coarser fishbone-shaped α-Al₁₅(Fe, Mn)₃Si₂ phases are observed in its microstructure. As the Mn/Fe ratio increased to 0.7, blocky and Chinese script-, or fishbone-shaped compounds as the main intermetallic compounds found in the microstructure of the A2 alloy.

Acknowledgements

The authors acknowledge funding for this research from National Science Foundation of China (51261011), Science and Technology Project Foundation of Yunnan Province of China (2010DH025), and Personnel Training Project of Yunnan Province of China (2009CI024). This work is supported by the Institute of Advanced Materials Processing, Kunming University of Science and Technology, Kunming, China.

Received: August 17, 2013

Revised: October 25, 2013

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Publication Dates

• Publication in this collection
  06 Dec 2013
• Date of issue
  Apr 2014

History

• Accepted
  25 Oct 2013
• Received
  17 Aug 2013