Trans. Nonferrous Met. Soc. China 30(2020) 1826-1838

Multiple eutectic orientation relationships in undercooled Ni-38wt.%Si eutectic alloy

Fan ZHANG¹, Hai-feng WANG¹, Cun LAI², Jian-bao ZHANG¹, Ya-chan ZHANG¹, Qing ZHOU¹

1. Center of Advanced Lubrication and Seal Materials, State Key Laboratory of Solidification Processing, Northwestern Polytechnical University, Xi’an 710072, China;

2. The Third Academy of CASIC, Beijing 100074, China

Received 2 November 2019; accepted 8 June 2020

Abstract: Eutectic orientation relationships (EORs) in an undercooled Ni-38wt.%Si alloy were analyzed by electron backscatter diffraction. A total of seven EORs were identified, and three of them were found at the under-cooling degree DT≈31 K. It is found that their orientations of the primary NiSi phase are same but the misorientation between the neighboring NiSi₂ grains can be either 50° or 60°. The multiple EORs were ascribed to a possible change in the growth direction of the primary phase, the change of the primary phase from the NiSi phase to the NiSi₂ phase, and the transition from coupled to uncoupled eutectic growth. The current work shows that epitaxial growth of the second eutectic phase on the primary eutectic phase can obey either a single EOR or multiple EORs, which is a unique phenomenon.

Key words: eutectic orientation relationship; epitaxial growth; undercooling; Ni-Si alloy

1 Introduction

Eutectic alloys have been studied intensively by experiments and modeling due to their practical and theoretical importance [1-9]. Recently, much attention has been paid to the eutectic orientation relationship (EOR) [10-24]. EOR is strongly related to the growth mechanism and thus greatly influences the microstructure and mechanical properties of eutectics. Regarding ceramic oxide eutectics, RAMIREZ-RICO et al [10] studied the texture resulting from the directional solidification of Al₂O₃-ZrO₂ (Y₂O₃) system and found that the phases grow according to the relationship For directional solidification of NiO-YSZ, CoO-YSZ, NiO-CeO₂, NiO-GDC, CoO-CeO₂ and CoO-GDC eutectic systems, ZABALETA et al [11] found two EORs, and the most common of them is (111)_TMO//(001)_IC, (TMO=NiO, CoO; IC=YSZ, GDC, CeO₂). As one of the most widely used systems for modeling studies of eutectic growth, the Al-Al₂Cu eutectics formed during directional solidification possess a common EOR of , [12], i.e., the so-called “Beta 6” relationship [13]. Since the Al-Al₃Ni eutectics could play an important role in thermally stable shape cast alloys and could potentially make aligned fiber composite materials for high-strength applications, their crystallographic orientations and formation mechanisms have been studied [14], and their EOR was found to be , [15].

Owing to the superior castability, lightmass, high wear resistance and good corrosion resistance, the Al-Si alloys are the most widely used aluminum casting alloys [19]. One of the important ways to improve their strength and ductility is to change the morphology of the eutectic Si (i.e., from a coarse plate-like microstructure to a fine fibrous microstructure) by adding certain elements (e.g., Sr and Sc) [16-19]. Four types of direction parallelisms between the eutectic α(Al) and the eutectic Si have been reported, i.e., <001>_Al//<110> _Si, <001>_Al//<001> _Si, <112>_Al//<112> _Si and <112>_Al//<110> _Si. The other way to control the EOR and the eutectic morphology is to modify the processing process. For directional solidification of eutectic alloys, LI et al [21-23] carried out a series of studies to determine the effects of a high magnetic field on the morphologies and orientations of the primary phase and the eutectic phases. Taking the Al-Al₃Ni eutectic alloy as an example, the EOR changes from , without a magnetic field to and with a high magnetic field [21].

The investigation was also done to characterize the EORs of ternary eutectics [24]. For directional solidification of an Al-Ag-Cu alloy, two different sets of EORs were identified among the α(Al), Al₂Cu and Ag₂Al phases, i.e., and {130}_Al // The less common EOR of was found in the ternary Al-Ag-Cu alloy, indicating that the presence of the Ag₂Al phase stabilizes this particular EOR.

All of the previously mentioned researches on EORs [10-24] focused on directional solidification and casting, and in this case, the growth velocity is small, and the interface is under local equilibrium conditions. However, with an increase in velocity, the interface becomes under non-equilibrium conditions, leading to the significant changes in the interface dynamics and the eutectic morphologies [1]. It should be noted that the non-equilibrium solidification is a useful method to control and enrich eutectic microstructures. For example, an important non-equilibrium phenomenon in undercooled eutectic alloy melts is the transition from regular lamellar to anomalous eutectics [5-9]. Taking into account the important role of orientation relationships on eutectic growth [10-25], the present work aimed at reporting the EORs in undercooled alloys.

In this work, the EORs in undercooled Ni-38wt.%Si alloy, with two stoichiometric intermetallic compounds (i.e., NiSi and NiSi₂ [15]) as eutectic products, were identified by using the electron backscatter diffraction (EBSD). For the Ni-38wt.%Si eutectic alloy with different undercooling degrees and microstructures, the interplay relationships between the EORs and the eutectic morphologies were discussed. Special attention was paid to the growth mechanism of the eutectics. The present work shows that epitaxial growth of a second eutectic phase on the first eutectic phase can obey either a single EOR or multiple EORs and helps understand eutectic growth and eutectic morphologies.

2 Experimental

A high-purity ingot with a mass of approximately 50 g and a nominal eutectic composition of Ni-38wt.%Si was prepared from pure nickel (99.99%) and silicon (99.999%). The melt flux technique was used to undercool the Ni-38wt.%Si eutectic alloy. A quartz-glass crucible, which was rinsed previously in an alcoholic solution by an ultrasonic cleaning machine, was used as the container. The master alloy was re-melted at least three times in an arc furnace under a high-purity Ar atmosphere to ensure chemical homogeneity. A sample with mass of approximately 2 g was cut from the master alloy, and then placed into the quartz-glass crucible with a certain quantity of boron oxide glass flux. The quartz-glass crucible was positioned within the high-frequency induction coil of a chamber that was first evacuated to a pressure of 3×10^-3 Pa and then backfilled with high-purity Ar gas to a pressure of 5×10^-2 MPa. The sample, covered by the melt flux, was heated to 100-250 K above the eutectic temperature and held at that temperature for approximately 20 min. Each sample was cyclically superheated and cooled until the desired undercooling degree was achieved.

The as-solidified sample was mounted in Bakelite and carefully polished. After etching in a solution of 10 mL H₂O₂, 10 mL HCl, and 50 mL H₂O, the sample was observed with an optical microscope (Olympus GX71) to examine various eutectic microstructures. After polishing the sample with a SiO₂ colloidal suspension in a vibratory polisher, the crystallographic orientations were studied using a scanning electron microscope (TESCAN MIRA 3 XMU) equipped with an EBSD analysis system. Using the software Channel 5 Suite and Material Studio 8.0, the models for the spatial distribution of the lattices were established to examine the EORs directly.

Since the compositions of eutectic products, NiSi and NiSi₂ phases, do not change with undercooling degree, the chemical superheating effect [26] is eliminated, and the reduction of interfacial energy is left as the only driving force for re-melting. Furthermore, there is no phase transformation except for eutectic solidification in this alloy system. Consequently, the initial eutectic solidification microstructures can be completely or at least partially retained to room temperature to identify the EORs that occur during non-equilibrium solidification.

3 Results

The maximal undercooling degree achieved in the present work is DT≈74 K. To examine the microstructure evolution, the as-solidified sample with an undercooling degree interval of approximately 5 K was retained to room temperature. Five different microstructures were found among undercooling degrees of approximately 3, 15, 31, 51 and 74 K. The EOR is generally demonstrated by the parallel crystal plane and the parallel crystal direction in the parallel crystal plane [10-24]. According to the geometry of pole figures (PFs), if the poles overlap in the PFs of two eutectic phases, their corresponding lattice planes or crystal orientations are parallel. EBSD was used to characterize the crystallographic orientations of the NiSi and NiSi₂ phases to determine the EORs for the five different microstructures, as seen in Figs. 1-7, in which the parallel crystal planes and directions between the NiSi and NiSi₂ phases are depicted using the software Channel 5 Suite and Material Studio 8.0, and the large and small spheres represent the Ni and Si atoms, respectively.

3.1 Single EOR at DT≈3 K

For DT≈3 K, the microstructure of the Ni-38wt.%Si eutectic alloy is a typical thin and regular lamellar eutectic (Figs. 1(a₁) and (a₂)). From the EBSD orientation maps, only one main orientation was found for the NiSi (Fig. 1(a₁)) and the NiSi₂ (Fig. 1(a₂)) phases, which is consistent with the cooperative growth of lamellar eutectics. For the PFs of the NiSi and NiSi₂ phases in Figs. 1(b₁) and (b₂), there is an overlap between {110}_NiSi and and , indicating that the corresponding EOR is {110}_NiSi//{112}_NiSi2, The fore- named EOR is demonstrated by the families of the crystal planes and directions. A model for the spatial distribution of the lattices needs to be established to obtain the parallel crystal plane and the parallel crystal direction in the parallel crystal plane. Figures 1(c₁) and (c₂) show schematic diagrams of the EOR at DT≈3 K. The pink crystal plane and crystal direction are the parallel crystal plane and parallel crystal direction in the parallel crystal plane, i.e., . In this case, only one single EOR can be identified.

3.2 Single EOR at DT≈15 K

For DT≈15 K, a directional and granular primary NiSi phase is surrounded by a thin and regular lamellar eutectic (Figs. 2(a₁) and (a₂)). From the EBSD orientation maps and PFs, three orientations can be found for the primary NiSi phase. Since the granular structures and the surrounding regular lamellae of the NiSi phase share the same orientation, the lamellar eutectics are formed by an epitaxial growth mechanism. Correspondingly, the regular lamellae of the NiSi₂ phase also have three orientations. The differences among the three orientations are not large (≤5°), and thus it is reasonable to integrate them into one orientation. Using this approach, only one orientation can be found for the NiSi (Fig. 2(a₁)) and NiSi₂ (Fig. 2(a₂)) phases, and there is an overlap between and and and (Figs. 2(b₁) and (b₂)), indicating that the corresponding EOR is Figures 2(c₁) and (c₂) show the schematic diagrams of the EOR at DT≈15 K. The blue crystal plane and crystal direction are the parallel crystal plane and parallel crystal direction in the parallel crystal plane, i.e., Only one EOR can be identified.

Fig. 1 EBSD orientation maps and eutectic orientation relationships of Ni-38wt.%Si alloy at DT≈3 K

3.3 Triple EORs at DT≈31 K

For DT≈31 K, the primary NiSi phase is surrounded by a coarse eutectic structure, and the rest of the microstructure is composed of a thin and regular lamellar eutectic, as seen in the EBSD orientation maps in Figs. 3(a) and (c). The {100} PFs are shown in Figs. 3(b) and (d). For the NiSi phase, only one orientation can be identified (Fig. 3(b)), indicating that both the coarse eutectic structures and the thin and regular lamellar eutectics are formed by epitaxial growth after the solidification of the primary NiSi phase (Fig. 3(a)). For the NiSi₂ phase, however, three main orientations can be found, and the orientation differences between them are rather large (Figs. 3(c) and (d)). The blue, green and pink grains are labeled as “A”, “B” and “C”, respectively, in Fig. 3(c). The blue and green (and the green and pink) grains share one concentrated pole in the {100} PF (Fig. 3(d)). Three other grains are labeled “A’”, “B’” and “C’”. The orientation differences among grains A, B, and C and grains A’, B’, and C’, respectively, are so small (≤ 5°) that they are not considered in the following analysis of EORs. These EBSD results suggest that there are three different EORs when DT≈31 K. Since the NiSi₂ grains are rather large (>200 mm), such three EORs should be formed by the eutectic solidification itself and should not be a result of re-melting, convection or solidification stresses that could considerably change the grain orientations [27-32].

Fig. 2 EBSD orientation maps and eutectic orientation relationships of Ni-38wt.%Si alloy at DT≈15 K

To determine the EORs, PFs of the NiSi and NiSi₂ phases when DT≈31 K are shown in Fig. 4. For the NiSi phase from Fig. 3(a) and grain A from Fig. 3(c), there is an overlap between {100}_NiSi and (Fig. 4(a₁)), <010>_NiSi and (Fig. 4(a₂)), indicating that the corresponding EOR is Similarly, the EORs between the NiSi phase from Fig. 3(a) and grains B and C from Fig. 3(c) are and as seen in Figs. 4(b₁), (b₂) and Figs. 4(c₁), (c₂), respectively. Figure 5 shows the schematic diagrams of the three EORs when DT≈ 31 K. For the NiSi phase from Fig. 3(a) and grain A from Fig. 3(c), the blue crystal plane and crystal direction are the parallel crystal plane and parallel crystal direction in the parallel crystal plane (Figs. 5(a) and (b₁)), i.e., Similarly, the green crystal plane and crystal direction correspond to the NiSi phase from Fig. 3(a) and grain B from Fig. 3(c), and the EOR is , ; the pink crystal plane and crystal direction correspond to the NiSi phase from Fig. 3(a) and grain C from Fig. 3(c), and the EOR is , as seen in Figs. 5(a), (b₂) and (b₃), respectively. Three EORs co-exist in the same sample when DT≈31 K. The green crystal planes in Figs. 5(a) and (b₂) are not easily distinguished due to the viewing angle. The orientation differences between the three NiSi₂ grains A, B and C can be obtained from the misorientation between the neighboring grains. For grains A and B (B and C), which share one concentrated pole in the {100} PF (Fig. 3(d)), the misorientation is approximately 50°. For grains A and C, which do not share a concentrated pole in the {100} PF (Fig. 3(d)), the misorientation is approximately 60°.

Fig. 3 EBSD analysis of eutectic microstructure in undercooled Ni-38wt.%Si alloy at DT≈31 K

Fig. 4 Three eutectic orientation relationships in undercooled Ni-38wt.%Si alloy at DT≈31 K

Fig. 5 Schematic diagrams of three EORs in undercooled Ni-38wt.%Si alloy at DT≈31 K

3.4 Single EOR at DT≈51 K

For DT≈51 K, strip-shaped NiSi structures and dendritic NiSi₂ grains are found as well as the thin and regular lamellar eutectics (Figs. 6(a₁) and (a₂)). From the EBSD orientation maps and PFs, only one orientation can be found for the NiSi (Fig. 6(a₁)) and NiSi₂ (Fig. 6(a₂)) phases, and there is an overlap between and (Fig. 6(b₁)), and (Fig. 6(b₂)), indicating that the corresponding EOR is The schematic diagrams of EOR when DT≈51 K are shown in Figs. 6(c₁) and (c₂). The green crystal plane and crystal direction are the parallel crystal plane and parallel crystal direction in the parallel crystal plane, i.e., . When DT≈51 K, only one EOR can be found.

3.5 Single EOR at DT≈74 K

Fig. 6 EBSD orientation maps and eutectic orientation relationships of Ni-38wt.%Si alloy at DT≈51 K

When DT≈74 K, re-melting induces anomalous eutectics that make the orientations random, aside from which only one orientation was found for the NiSi and the NiSi₂ phases, as seen in Figs. 7(a₁) and (a₂). As previously mentioned, the eutectic products of undercooled Ni-38wt.%Si alloy are two stoichiometric intermetallic compounds (i.e., NiSi and NiSi₂) [25], whose compositions do not change with undercooling degree. Consequently, the initial eutectic microstructure can be completely or at least partially retained to room temperature to exhibit the original EOR that governs non-equilibrium solidification. As shown in Figs. 7(b₁) and (b₂), the corresponding EOR is Figures 7(c₁) and (c₂) show the schematic diagrams of the EOR of Ni-38wt.%Si alloy when DT≈74 K. The red crystal plane and crystal direction are the parallel crystal plane and parallel crystal direction in the parallel crystal plane (Figs. 7(c₁) and (c₂)), i.e., Only one EOR can be identified.

All of the microstructures and the EORs characterized in the present work are summarized in Table 1. There are no identical EORs for different undercooling degrees with different microstructures. When DT≈15 and 31 K, the second NiSi₂ phase grows epitaxially on the primary NiSi phase (Figs. 2 and 3). Since the regular lamellar eutectics are formed during the post-recalescence stage when DT≈3, 15 and 31 K [9], their growth mechanisms and EORs should be the same, but this is not the case. When DT≈51 K, strip-shaped NiSi structures and dendritic NiSi₂ grains co-exist (Fig. 6). In this case, the epitaxial growth of the NiSi phase on the NiSi₂ phase and epitaxial growth of the NiSi₂ phase on the NiSi phase occur concurrently. Two different EORs are expected, but in fact, only one EOR can be found. When DT≈74 K, the epitaxial growth of the NiSi phase on the NiSi₂ dendrites forms a eutectic-dendrite, and an additional EOR is found. The current multiple EORs in the undercooled Ni-38wt.%Si eutectic alloy seem quite anomalous. It should be noted that when DT≈15 and 74 K, points in the PFs of NiSi and NiSi₂ phases are rather large which might determine current EORs plausible (see Figs. 2 and 7). Actually, with the help of the software Channel 5, we can find that the PFs of neighboring NiSi and NiSi₂ grains and the EORs are the same as what shown in Figs. 2 and 7.

Fig. 7 EBSD orientation maps and eutectic orientation relationships of Ni-38wt.%Si alloy at DT≈74 K

Table 1 Microstructures and EORs in undercooled Ni-38wt.%Si alloy

4 Discussion

4.1 EORs vs eutectic morphologies

For dendritic growth that involves only one kind of bulk phase and interface, the morphology is strongly related to the interface dynamics, and it is well known that the anisotropy of interface energy plays an important role in pattern formation [1]. Since the interface energy is different for different interface planes, the anisotropy of interface energy can be reflected in the growth direction. For example, several dendrite orientations have been identified in undercooled Cu-8.9wt.%Ni alloys, i.e., fully <100>-oriented at low undercooling degree, mixed <100>/<111>-oriented at intermediate undercooling degree and fully <111>-oriented at high undercooling degree [33,34]. The existence of competing anisotropies in different growth directions at intermediate undercooling degree gives rise to seaweed dendrite, which is characterized by its containment within a diverging split primary dendrite branch. In addition to the anisotropy of the interface energy, kinetic anisotropy also plays an important role in pattern formation [35] and can dominate if deviations from the local equilibrium conditions are significant. Therefore, the dendrite morphology might be influenced by two factors during non-equilibrium solidification, which are the anisotropy of the interface energy and the kinetic anisotropy.

Eutectic growth involves not only bulk phases and interfaces but also triple-junctions [3]. Taking the solidification of binary eutectics L→α+β as an example, there are three kinds of bulk phases (two solids, α and β, and one liquid, L), three kinds of interfaces (α/L, β/L and α/β) and one kind of triple-junction (α/β/L). Similar to dendrites, the interface dynamics plays an important role in pattern formation [36], and the anisotropy of the interface energies and the kinetic anisotropy should be considered simultaneously for non-equilibrium solidification of eutectic alloys. The dendrites have only one kind of solid/liquid interface, while there are two kinds of solid/liquid interfaces in the solidification of a binary eutectic, the α/L and β/L interfaces, for which the anisotropies of the interface energies can determine the growth directions. Furthermore, there is also one solid/solid interface, i.e., the α/β interface, whose interface energy anisotropy can be reflected by the EOR.

There is one kind of triple-junction, α/β/L. Recent work has shown that the triple-junction possesses specific line energy [37], which is different for different crystallography of tri-crystals [38], similar to the interface energy. For eutectic solidification, various eutectic patterns are considerably influenced by the kinetics of triple-junctions. One example is the experimental study of the CBr₄-C₂Cl₆ eutectic system [39,40]. In contrast to the classical stability theory [41,42], a lamellar pattern can be stable with a lamellar spacing that is smaller than that predicted by the minimum undercooling principle. Although the deviation of the contact angles from the eutectic interface normal direction is too small (e.g., 1°) to be detected, its significant effect on the stability is precisely measurable [40]. If triple-junctions are allowed to grow in not only normal but also lateral directions, the overstability of lamellar eutectic growth can be successfully explained [39,40].

The eutectic morphology might be controlled by eight separate factors during non-equilibrium solidification, which include the anisotropies of the interface energies and the kinetic anisotropies of the α/L, β/L and α/β interfaces and the anisotropy of the line energy and the kinetic anisotropy of the α/β/L triple-junction. Since the EOR is only one of the eight factors that may influence the eutectic morphology, it helps understand the eutectic microstructures but cannot be assumed to be the only factor that dominates the eutectic morphologies.

In the present work, the EORs are different for different eutectic microstructures. When DT≈15 and 31 K, the eutectic NiSi phase grows epitaxially from the primary NiSi phase, and then the eutectic NiSi₂ phase grows epitaxially from the eutectic NiSi phase, as seen in Figs. 2 and 3. When DT≈ 74 K, the NiSi phase grows epitaxially from the primary NiSi₂ phase, as seen in Fig. 7. Both the lamellar eutectics seen when DT≈15 and 31 K and the eutectic dendrites seen when DT≈74 K follow an epitaxial growth mechanism that obeys a specific EOR or EORs. The random orientation seen when DT≈74 K should be a result of re-melting, convection or solidification stresses [27-32] and cannot be taken as the characteristic of eutectic growth. When DT≈3 K, no primary phase is seen (Fig. 1), and when DT≈51 K (Fig. 6), both epitaxial growth of the NiSi phase on the NiSi₂ phase and epitaxial growth of the NiSi₂ phase on the NiSi phase are seen, a specific EOR is also available. The present work and the previous work on EORs [10-24] show that eutectic growth obeys the specific EORs and the EORs significantly influence the eutectic morphologies. It should be noted that no globally representative EOR is identified for either the unmodified or Sr-modified Al-12.7wt.%Si alloys in the work of LIU et al [19], according to which crystallographic compatibility across the phase interface is not a prerequisite for the formation of Al-Si eutectics. A detailed study of Fig. 6(b) in Ref. [19], however, indicates that there are multiple EORs between α(Al) and Si, similar to the case when DT≈31 K in the current study.

4.2 Multiple EORs vs single EOR

As stated in the introduction section, there are usually multiple EORs between two eutectic phases rather than just one, and under the effects of a high magnetic field, the EOR can change from one to another. In the present work, seven EORs are found between the NiSi and NiSi₂ phases and one case presents multiple EORs. For the lamellar eutectics seen when DT≈3, 15, 31 and 51 K, coupled eutectic growth prevails, whereas for the eutectic dendrites seen when DT≈74 K, uncoupled eutectic growth occurs [9]. Therefore, the possible change in the growth direction of the primary phase in undercooled melts [33,34], the change of primary phase from the NiSi phase to the NiSi₂ phase, and the transition from coupled eutectic growth to uncoupled eutectic growth can be the reasons for the current multiple EORs. For example, after nucleation or epitaxial growth of one eutectic phase, the epitaxial growth of the second eutectic phase depends not only on the phase but also on the orientation of the primary eutectics, thus significantly influencing the dominated EOR.

A single EOR or multiple EORs can be dominant, possibly depending on the crystallo- graphic character of the primary eutectic phase. In the present work, a single EOR is found when DT≈3, 15 and 74 K, and three EORs are found when DT≈31 K. To the best of authors’ knowledge, multiple EORs in one sample were reported for directional solidification or casting of unmodified and modified Al-Si alloys [16-19], where twin-controlled growth of the eutectic Si phase occurred on the primary Al phase. Since the twinning relationship is found within either a dendritic [18] or lath-shaped [19] Si grain, whereas grains A, B and C in Fig. 3 of the present work belong to different grains, the present triple EORs seem to be unique. In the case of a Mg-modified Nb-Si alloy [20], there are total eleven EORs in one sample; since the eutectic reaction is followed by a eutectoid reaction, it is not possible to retain the primary solidification microstructure that shows the original EORs during solidification. In contrast, the current work shows, without any controversy, that epitaxial growth of the second eutectic phase on the primary eutectic phase can obey either a single EOR or multiple EORs and thus helps understand eutectic growth and eutectic morphologies.

5 Conclusions

(1) There are multiple EORs in the undercooled Ni-38wt.%Si eutectic alloy and seven EORs are characterized in five different microstructures. Three EORs co-exist when DT≈ 31 K, in which the orientation of the primary NiSi phase is the same but the misorientation between the neighboring NiSi₂ grains can be either 50° or 60°. There is however no clear relationship between undercooling and the EOR(s).

(2) The EORs for the epitaxial growth of the NiSi phase on the NiSi₂ phase and the epitaxial growth of the NiSi₂ phase on the NiSi phase can be the same if the magnitude of undercooling is the same. The EORs of epitaxial growth of the NiSi phase on the NiSi₂ phase can be different and diverse if the magnitude of undercooling (or microstructure) is different, even for cases where the solidification conditions are similar.

(3) A possible change in the growth direction of the primary phase in undercooled melts, the change of the primary phase from the NiSi phase to the NiSi₂ phase, and the transition from coupled to uncoupled eutectic growth are the reasons for the current multiple EORs. The current work shows, without any controversy, that epitaxial growth of the second eutectic phase on the primary eutectic phase can obey either a single EOR or multiple EORs. Such a phenomenon is unique in our understanding of cooperative growth, further theoretical analysis of which will improve current eutectic growth theory and might play an important role in microstructural control.

(4) Though both the present work and previous work on EORs show that eutectic growth obeying specific EOR(s) and the EOR(s) can significantly influence the eutectic morphologies, the EOR is only one of the eight factors that may influence the eutectic morphologies. It helps understand the eutectic microstructures but cannot be assumed to be the only effect that dominates eutectic morphologies.

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过冷Ni-38%Si共晶合金中的多重共晶取向关系

张 帆¹，王海丰¹，赖 存²，张建宝¹，张雅婵¹，周 青¹

1. 西北工业大学 凝固技术国家重点实验室 先进润滑与密封材料研究中心，西安 710072；

2. 中国航天科工集团公司第三研究院，北京 100074

摘 要：采用电子背散射衍射技术分析过冷Ni-38%Si(质量分数)合金中的共晶取向关系，发现在过冷Ni-38%Si (质量分数)合金中总共存在7种共晶取向关系。当过冷度DT≈31 K时，存在3种共晶取向关系，其初生NiSi相的取向相同，但相邻NiSi₂晶粒之间的取向差约为50°或60°。多重共晶取向关系的产生归因于初生相生长方向的变化、初生相从NiSi相到NiSi₂相的变化以及生长方式从耦合共晶生长到非耦合共晶生长的转变。第二共晶相外延生长于初生共晶相时可以遵循一种共晶取向关系或多种共晶取向关系，这是一种较为独特的现象。

关键词：共晶取向关系；外延生长；过冷；Ni-Si合金

(Edited by Wei-ping CHEN)

Foundation item: Project (2018-JC007) supported by the Science Fund for Distinguished Young Scholars from Shaanxi Province, China; Project (3102017HQZZ008) supported by the Fundamental Research Funds for the Central Universities, China

Corresponding author: Hai-feng WANG; Tel: +86-13519186961; E-mail: haifengw81@nwpu.edu.cn

DOI: 10.1016/S1003-6326(20)65342-0