Crystallographic features of the martensitic transformation and their impact on variant organization in the intermetallic compound Ni50Mn38Sb12 studied by SEM/EBSD

The martensitic transformation orientation relationship (OR), the transformation deformation and their impact on variant organization in an Ni50Mn38Sb12 alloy have been thoroughly studied by scanning electron microscopy/electron backscatter diffraction (SEM/EBSD), as they are decisive factors for mechanical and magnetic properties. The transformation OR has been identified and the consequent hierarchical organization of martensite variants has been fully revealed.


Introduction
The martensitic transformation is a diffusionless solid-state phase transition occurring in alloys, mainly steels, and intermetallic compounds. During the transformation, the structural change from the parent phase to the product phase is realised by a coordinated lattice deformation. To ensure minimum energy consumption, the resultant martensite is usually selfaccommodated in terms of transformation strain and possesses invariant habit planes with the parent austenite. Owing to the fact that the properties of alloys can be optimized by martensitic transformation through microstructure modification, the martensitic transformation is still a topic of intensive experimental and theoretical studies. Investigations have been conducted mainly on transformation microstructure characteristics (Maresca et al., 2016;Wang et al., 2016;Zhang, Ruimi et al., 2016), phase transition features (Hilkhuijsen et al., 2013;De Knijf et al., 2014;Zolotorevsky et al., 2015) and property optimization (Zhen et al., 2015;Findley et al., 2017).
Other than the various steels, many intermetallic compounds, such as shape-memory materials (NiTi, and Cubased and Fe-based alloys), also exhibit a martensitic transformation. This transformation is reversible in shape-memory alloys, allowing a recovery of the shape change induced by the forward transformation. Recently, it has been revealed that the newly developed magnetic Ni-Mn-X (X = Ga, In, Sn, Sb) Heusler-type intermetallic compounds exhibit a martensitic transformation. Moreover, the structure transformation is always accompanied by a magnetic transition, giving rise to a variety of novel magnetic field-driven phenomena. Many studies have been conducted on the exploration of new properties and the characterization of microstructures resulting from the martensitic transformation (Sozinov et al., 2002;Khovailo et al., 2003;Sutou et al., 2004;Krenke et al., 2005;Pasquale et al., 2005;Cong et al., 2007;Khan et al., 2007;Krenke et al., 2007;Babita et al., 2009;Monroe et al., 2012;Yu et al., 2014;Huang et al., 2015;Yang et al., 2015;Sharma et al., 2016a,b).
As a new member of this family, the Ni-Mn-Sb system has demonstrated multiple functionalities under an actuating magnetic field, such as the shape-memory effect (SME) (Yu et al., 2014), the magnetocaloric effect (MCE) (Nayak et al., 2009;Akkera et al., 2015;Barman & Kaur, 2015), giant magnetoresistance (GMR) (Khan et al., 2013;Sahoo et al., 2013) and exchange bias (EB) (Sharma Akkera et al., 2013;Lee et al., 2013;Barman et al., 2014). These materials have thus been considered as potential candidates for magnetic shapememory, magnetic refrigerant and magnetic recording applications. It has been shown that, for the Ni-Mn-Sb system, the occurrence of SME, MCE, GMR and EB is closely related to the martensitic transformation. It has been proved that, by modifying the transformation process, the properties can be considerably improved. For example, Nayak et al. (2009) applied a 1.1 kbar (1 bar = 100 000 Pa) pressure to a polycrystalline Ni 45 Co 5 Mn 38 Sb 12 alloy during the forward and reverse martensitic transformation processes and obtained a significant increase in entropy from 41.4 to 46 J kg À1 K À1 . Such an enhancement was speculated to be the result of a reorientation of the martensite variants from the original astransformed microstructure of martensite, driven by the external pressure. However, information concerning the variant organization in the as-transformed microstructure, crystallographic features of the martensitic transformation and their impact on variant organization is still missing. This information is essential for a deep understanding of the specific functionality of these materials and hence serves as a prerequisite for further development of these materials towards practical applications.
In the present work, a thorough experimental examination and crystallographic analysis was conducted on the organization characteristics of the resultant martensite variants, the orientation relationship (OR) of the martensitic transformation and the transformation strain characteristics of an Ni-Mn-Sb alloy, with the aim of working out the underlying mechanisms of the specific variant organization features. High-resolution scanning electron microscopy (SEM) electron backscatter diffraction (EBSD) characterization was utilized to acquire the spatially correlated microstructural and crystallographic orientation information of the martensite variants. The formation mechanism of the martensite microstructure was investigated by analysing the transformation strain compatibility of adjacent martensite variants. This study is expected to provide comprehensive fundamental crystallographic and microstructural information on Ni-Mn-Sb intermetallic compounds for further studies.

Materials and experimental details
A polycrystalline Ni-Mn-Sb alloy with the nominal composition Ni 50 Mn 38 Sb 12 (at.%) was used in the present work. The alloy was prepared by arc melting high-purity elements Ni (99.99 wt%), Mn (99.8 wt%) and Sb (99.995 wt%). An extra 2% (wt%) Mn and an extra 2% (wt%) Sb were added to compensate for the weight loss due to the excessive volatilization of these two elements. The ingot was re-melted four times to ensure a homogeneous composition and then spray cast into copper moulds to obtain dense bulk cylindrical samples. The samples were annealed at 1173 K for 24 h followed by water quenching for compositional homogeneity. The arc melting, spray casting and heat treatment were carried out under an argon atmosphere. The actual chemical composition of the prepared alloy analysed by energy dispersive spectrometry is Ni 49.43 Mn 38.07 Sb 12.50 (at.%), very close to the nominal composition. The martensitic transformation start and finish temperatures, and the austenitic transformation start and finish temperatures, of the present alloy are 314.94 and 308.85 K, and 328.17 and 334.05 K, respectively (Zhang, Yan et al., 2016). This indicates that at room temperature the alloy is in the martensite state.
To investigate the microstructure of the martensite and the crystallographic characteristics of the martensitic transformation, parallelepiped samples with sizes of 4 Â 6 Â 10 mm were cut out of the annealed cylindrical samples by electrical discharge wire-cutting. The samples were mechanically ground with SiC papers and electrolytically polished using a solution of 20% nitric acid and 80% methanol (v/v). The electrolytic polishing was conducted at 273 K under a continuous multistep mode: 8 V for 10 s, 15 V for 5 s and 18 V for 3 s.
The microstructural and crystallographic characterizations were performed using a field emission gun SEM (JEOL 6500F) equipped with an EBSD acquisition camera (Oxford) and the Aztec online acquisition software (Oxford Instruments). Both manual and automatic modes were used for orientation acquisition. Crystallographic calculations, e.g. pole figures, misorientation, trace analysis and coordinate transformation, were applied in the crystallographic analyses.

Morphological features of 4O martensite
At room temperature, the present alloy is composed of 4O modulated martensite. Fig. 1 shows a typical backscattered electron (BSE) micrograph of the martensite in Ni 50 Mn 38 Sb 12 . It is seen that the martensite is organized hierarchically from sub-micrometric lamellae to micrometric plates (outlined by the yellow dashed lines in Fig. 1a) and from plates into plate groups (outlined by the blue dashed lines in Fig. 1a). Within each plate, the fine lamellae stretch roughly in the same direction, and within each plate group the plates also stretch in almost the same direction and share an almost straight plate interface, as marked by the black dashed line in Fig. 1(a). For easy reference, we denote the groups of almost-parallel plates a 'plate colony' and the plate of lamellae a 'variant colony'. It can be seen that, in some plate colonies (for example C 1 in Fig. 1a), the traces of the plate interfaces are parallel, whereas in others (for example C 2 and C 3 ), the traces are not exactly parallel but deviate one from another by a maximum of 5 , as highlighted in Fig. 1(a). Fig. 1(b) displays the magnified BSE image of one plate colony (C 1 ) of Fig. 1(a). It is seen that, within the plate colony, the orientation of the lamellar interface trace changes from plate to plate. Each plate colony is composed of four distinct plates in terms of lamellar interface trace orientation, indicated by P 1 -P 4 in Fig. 1(b).

Crystallographic correlations between martensite variants
3.2.1. Intra-plate variants. Further EBSD orientation analysis demonstrated that, within each plate, there are four distinct orientation variants, A, B, C and D, as shown in Fig. 2. The four lamellar or intra-plate variants are related to one another by three kinds of twin relationship [type I twin (A/C and B/D), type II twin (A/B and C/D) and compound twin (A/D and B/C)], as fully determined in our previous work (Zhang, Yan et al., 2016). Moreover, the four intra-plate  Table 1 180 rotation (!, d) and the plane normal to the rotation axis d of the interplate variant pairs in plates P 1 and P 2 , and P 2 and P 3 .    . This plane is also their type I twinning plane K 1 . Close observation revealed that only type I and type II twin-related variants form the plate interfaces and type II twins appear in a majority. Compound twin-related variants occur only within plates.

Inter-plate variants.
Using the measured orientations of the variants in the four distinct plates in Fig. 1(b) (P 1 , P 2 , P 3 and P 4 ), the ORs between adjacent variants in neighbouring plates (connected by the plate interfaces P 1 /P 2 , P 2 /P 3 and P 3 /P 4 ) were analysed. As seen in Fig. 1(b), each variant in one plate can have four possible combinations with the four variants in the other plates. Hence, we calculated the misorientation (!, d) and the plane normal to the rotation axis d of all the possible variant pairs from plates P 1 to P 4 . The results show that, for any variant in plate P i (i = 1, 2, 3 and 4), there exists only one variant in the adjacent plate P i+1 (for i = 4, the adjacent plate is P 1 ) that has a 180 rotation relationship with it. The misorientations of such variant pairs are equivalent at all plate interfaces P i /P i+1 . Table 1 displays the results for the variant pairs at P 1 /P 2 and P 2 /P 3 . For easy notation, we denote the four distinct variants in plate We then studied the orientation character of the plane that is normal to the 180 rotation axis of each variant pair. Such a plane should be shared by the corresponding pair of variants. We found that, although the Miller indices of the plane change from pair to pair, the spatial orientations of these planes are very close. For the variant pairs at P 1 /P 2 and P 3 /P 4 , the orientations of these planes coincide with those of the plate interfaces P 1 /P 2 and P 3 /P 4 , as shown by the example P 1 /P 2 in Fig. 3(a). In the figure, these planes are represented by their stereographic projections in the macroscopic sample coordinate system, and their traces, as well as the P 1 /P 2 plate interface trace, are indicated by black solid lines. The deviation between these planes and the plate interface should be attributed to the experimental imprecision arising from the tilt of the sample for the EBSD measurement. This result indicates that the plate interface should be the mirror plane of the two variants that possess a 180 rotation at P 1 /P 2 and P 3 /P 4 . However, for the variant pairs at P 2 /P 3 and P 4 /P 1 , the orientations of the common planes are not coincident with those of the plate interfaces P 2 /P 3 and P 4 /P 1 but 90 away, as shown in Fig. 3(b). These inter-plate variant characteristics are confirmed to be the same for the other plate groups. Such characteristic variant organization features suggest that, during the martensitic transformation, P 1 -P 2 or P 3 -P 4 may form coordinately and grow coordinately. Plate interfaces P 2 /P 3 or P 4 /P 1 may form when the corresponding plates meet during the transformation. We denote the former plate interfaces 'compatible interfaces' and the latter plate interfaces 'incompatible interfaces'. Knowledge of the transformation ORs should be useful and allows further analysis of the organization features of the present martensite.

Determination of martensitic transformation OR
3.3.1. Crystal structure and structure simplification. As specified by our previous work, the martensite of Ni 50 Mn 38 Sb 12 (used in the present work) possesses a 4O (22)    3.3.2. Determination of transformation OR by crystallographic calculations. Generally, the transformation OR is defined by one pair of parallel crystalline planes and one pair of in-plane parallel directions from the corresponding parent and product phases. By consulting the literature, four representative ORs, namely the Bain (Bain & Dunkirk, 1924), the Kurdjumov-Sachs (K-S) (Kurdjumow & Sachs, 1930), the Nishiyama-Wassermann (N-W) (Nishiyama, 1934;Wassermann & Mitt, 1935) and the Pitsch (Pitsch, 1962) ORs, were selected as possible transformation ORs for the present alloy. By adapting the Miller indices of the published ORs to the structures of the present austenite and the average cell of the martensite, the plane and direction parallelisms defined by these ORs are as specified in Table 2.
The above microstructural observations of Ni 50 Mn 38 Sb 12 reveal that, at room temperature, the martensitic transformation is complete. All the parent austenite has transformed to the product martensite without any retained austenite. Thus, the OR is determined indirectly by inspecting the calculated orientations of the austenite from the measured orientations of the martensite variants originating from the same initial austenite grain under the four ORs listed in Table 2. The OR that ensures a common austenite orientation should be the effective one. Here we used the orientations of the four variants (A, B, C and D) displayed in Fig. 2(a) to determine the effective transformation OR. To ensure the accuracy of the determination, we used the mean orientation of the four martensite variants.
With the mean orientation of the four variants, the rotation matrix G A that expresses the orientation of the possible original austenite with respect to the sample coordinate system can be calculated via the assumed OR using the following equation: where G M is the rotation matrix representing the orientation of the martensite variant with respect to the sample coordinate system, S i M (i = 1-4) and S j A (j = 1-24) are the corresponding rotational symmetry matrices of the orthorhombic and cubic crystal systems, respectively, G MM is the coordinate transformation matrix from the orthnormal crystal coordinate frame set to the 4O modulated martensite to the orthnormal crystal  Table 2 Plane and direction parallelisms defined by the four ORs adapted to the structure of the austenite and the average structure of the present martensite.   coordinate frame set to the average unit cell of martensite, and G OR is the coordinate transformation matrix from the orthonormal crystal coordinate frame set to the average unit cell of martensite to the cubic coordinate system set to the lattice basis of austenite under a given OR listed in Table 2. The calculated orientations of the austenite are represented with their {001} A stereographic projections in the sample coordinate system and shown in Fig. 5. Due to the symmetry of the cubic system, one austenite orientation is represented with three distinct but equivalent {001} A poles that are marked with triangles of the same colour and orientation in the figures. The colours of the triangles are consistent with those of the martensite variants displayed in Fig. 2(a). Due to crystal symmetry, one measured martensite variant can generate several distinct austenite orientations depending on the OR. If the OR is effective for the transformation of the present alloy, the orientations of the austenite calculated from the four martensite variants should share a common austenite orientation. That means that each of the three {001} A poles from the corresponding variants should superimpose on the {001} A stereographic projection. It can be seen from Fig. 5 that, among all the selected ORs, only the Pitsch relation ensures a common austenite orientation from all the martensite variants, indicating that this OR could be the effective one. To quantify further the mismatch between the closest orientations of austenite calculated from the variants under the four ORs, the disorientation angles between each pair of austenite orientations were calculated and these are listed in Table 3 Table 4, thus giving rise to four distinct martensite variants. As the {221} M plane of the four variants that result from the common {011} A plane are parallel, these four variants are, in fact, those belonging to one variant plate, as revealed experimentally above (Fig. 2b).
With the determined OR between the austenite and the martensite, the interface between plates in each plate colony can be correlated with the planes of the austenite. As revealed by the above experimental results, the compatible plate interface is defined by the plane that is normal to the 180 rotation axis (listed in   Table 4 OR between the original austenite and the four martensite variants A, B, C and D shown in Fig. 2 Fig. 6(a). If we take the (011) A plane, i.e. the common plane in the two groups, as the compatible plate interface, two distinct compatible plate pairs can be constructed, as illustrated in Fig. 6(b). Each plate group contains two distinct compatible plate pairs and these two pairs correspond to the four distinct plates in one plate colony. This result is completely consistent with the observed microstructure features. Such a specific variant selection rule in a plate colony should be related to the transformation strain characteristics of the constituent variants and their interplay. Thus, analysis of the transformation strain is imperative to figure out the underlying mechanisms.

Transformation strain compatibility at plate
interfaces in plate colony. With the determined transformation OR, the structure deformation to form the martensite variants at the two kinds of plate interface within one plate colony were further calculated using the phenomenological theory of martensitic transformation (Wechsler et al., 1953;Bowles & Mackenzie, 1954;Ball & James, 1987;Jin & Weng, 2002;Bhattacharya, 2003;Balandraud et al., 2010) to examine their geometric compatibility at the two kinds of plate interface (compatible and incompatible). Here we take the variants in plates P 1 , P 2 , P 3 and P 4 in Fig. 1(b) for the compatibility analysis.
The deformation gradient tensor to describe the structure transformation from austenite to each corresponding martensite variant was established by examining the atomic correspondences of the original austenite and the variants under the Pitsch OR, as illustrated in Fig. 7. The deformation gradient tensor F or in the OR frame (xyz), can be constructed as follows: It can be further expressed in the Bravais lattice basis of austenite by a coordinate transformation Thus the deformation gradient tensors of the 24 theoretical variants can be calculated using the following equation: for i = 1-24, where S i A are the rotational symmetry elements of the cubic crystal system. Then, by examining the measured orientation of the 16 variants A i , B i , C i and D i (i = 1, 2, 3 and 4) in plates P 1 -P 4 in Fig. 1(b), we can obtain the deformation gradient tensors of the 16 variants in the four plates expressed in the Bravais lattice basis of austenite as listed in Table 5.
According to the phenomenological theory of martensitic transformation, the transformation is characterized by an invariant plane strain. In mathematics, if such a condition is achieved, one of the eigenstrains of the transformation deformation should be equal to 1. In reality, this means the transformation can produce an invariant interface between austenite and martensite, the so-called habit plane. For the present alloy, the eigenstrains of each single variant are 0.9458, 1.0165 and 1.0303, respectively. None of them equals 1. That means that, by forming a single martensite variant, the invariant plane strain condition cannot be satisfied. Thus locally, two twin-related variants are needed and a sandwichstructured variant agglomeration is usually formed to achieve an invariant habit plane. This corresponds exactly to what we observed in the microstructure. Thus, the total deformation  Table 5 Deformation gradient tensor F of variants in plates P 1 -P 4 in Fig. 1(b)  Lattice correspondences between the parent austenite (black) and the product martensite (red) under the Pitsch OR. gradient tensor of the paired variants F can be described by the following equation (Jin & Weng, 2002): Here, F M and F N are the deformation gradient tensors of the two constituent variants M and N, and is the volume fraction of variant M, enabling an invariant habit interface. The results of these calculations show that both the type I twin combination and the type II twin pair can form invariant habit planes. The volume fractions of the two pairs are 0.7201:0.2799 and 0.7179:0.2821, respectively, which are in good accordance with our experimental results.
With the above results, we further studied the transformation strain characteristics of different variant pairs in one plate colony. Here we take variant pairs A 1 /B 1 , A 2 /B 2 , C 3 /D 3 and C 4 /D 4 in plates P 1 , P 2 , P 3 and P 4 in Fig. 1(b) as examples. Variant pairs A 1 /B 1 and A 2 /B 2 (C 3 /D 3 and C 4 /D 4 ) form the compatible plate interface, and A 1 /B 1 and C 3 /D 3 (A 2 /B 2 and C 4 /D 4 ) the incompatible interface. The plate interface in the plate colony of Fig. 1(b) corresponds to (011) A . The deformation gradient tensors of the four variant pairs F A 1 B 1 , F A 2 B 2 , F C 3 D 3 and F C 4 D 4 are calculated and expressed in the ijk coordinate frame, as illustrated in Fig. 8, where the i axis is parallel to the intersection of the twinning plane of variant pair A 1 /B 1 on the plate interface (011) A , the k axis is normal to the plate interface (011) A and the j axis is the vector cross product of the two axes k and i: In the deformation gradient tensor, the three diagonal elements F(i, i), F(j, j) or F(k, k) represent normal contraction (<1) or elongation (>1) along the i, j or k axis, whereas the six off-diagonal elements represent shears [for example F(i, j) represents a shear in the i direction on the plane normal to j]. For variant pairs A 1 /B 1 and A 2 /B 2 (C 3 /D 3 and C 4 /D 4 ) connected by a compatible plate interface, the components of the two tensors F A 1 B 1 and F A 2 B 2 (F C 3 D 3 and F C 4 D 4 ) demonstrate a matched edge-to-edge deformation character. All the corresponding elements in the two tensors have exactly the same absolute value with the sign of the shear components F(i, k), F(j, k), F(k, i) and F(k, j) reversed. From Fig. 8, we can see that, under such a deformation manner, the two variant colonies keep a matched transformation deformation along the directions of i and j [the same F(j, i) and F(i, j)]. For the shear deformation either in the direction of k or on the plane normal to k, the sign of the strain is reversed. This keeps the deformation on the two sides of the plate interface symmetrical and balanced. Thus the transformation strain at the interface is totally compatible, ensuring a coordinated and compatible growth of the martensite variants in the two plates.
For variant pairs A 2 /B 2 and C 3 /D 3 (A 1 /B 1 and C 4 /D 4 ) that are connected by the incompatible plate interface, only the F(k, k) element has the same value whereas the others do not, suggesting that the plate interface should be formed when the two plates meet during the transformation process. In such a case, the normal strain F(k, k) and the two shear strains F(k, i) and F(k, j) in the k direction affect the orientation of the plate interface. As the two shear strains F(k, i) and F(k, j) from the two pairs of variants from the two plates are not totally symmetric, the orientation of the incompatible plate interfaces could deviate from that of the compatible plate interfaces. As the two shear strains are relatively small, the deviation should be small. Depending on the orientation of these interfaces with respect to the observing plane, the traces of the incompatible plate interfaces could be parallel to those of the compatible ones, as in the case of the colony in Fig. 1(b), or at certain angle, as in the case of plate colonies C 2 and C 3 in Fig. 1(a).
According to the symmetry of the cubic crystal system, one can have six equivalent {011} A planes, each of which can be associated with one plate colony. Thus in total, one original austenite grain can produce six distinct plate colonies. Our experimental observations revealed only three distinct plate colonies. As our microstructure observations were conducted on a two-dimensional sample section, it is possible that there are six distinct plate colonies in the three-dimensional space of austenite grains. To verify this hypothesis, we studied the overall transformation strain of the plate colonies to see if there is any request for strain accommodation between colonies. We can find, in Fig. 1(b), that the two distinct plates whose transformation strains are compatible at the plate interface (P 1 and P 2 , and P 3 and P 4 ) always possess the same width. Plate P 3 (and P 4 ) is about thrice as wide as plate P 1 (and P 2 ). Hence, we calculate the total deformation gradient of these four plates with the four calculated tensors of variant Illustration of the variant composition in the vicinity of the plate interface based on the morphological features described in Section 3.1 and Section 3.2. The ijk coordinate frame is orthonormal, with i parallel to the intersection line of the twinning plane of variant pair V P and V Q and the plate interface, k normal to the plate interface, and j the vector cross product of k and i. pairs A 1 B 1 , A 2 B 2 , C 1 D 1 and C 2 D 2 given in equations (6a)-(6d), using the following form: F ¼ 0:25 0:5F A 1 B 1 þ 0:5F A 2 B 2 À Á þ 0:75 0:5F C 1 D 1 þ 0:5F C 2 D 2 À Á From the tensor in equation (7) one can see that four of the six shear strains are zero. The remaining two shear strains, F(j, i) and F(i, j), are also very small compared with those in equations (6a)-(6d). For the three diagonal elements which represent the normal strains, they are very close to 1. This indicates that the transformation gradient of these four plates is very close to the identity matrix representing the original austenite. This means that, within each plate colony, the transformation strain is self-accommodated and there is almost no request for strain accommodation from other colonies. Hence, different plate colonies could form randomly in the original austenite grains. The plate colony interfaces should also form randomly when plate colonies meet during the transformation process. This explains why the plate colony interfaces are irregular, as outlined with the blue dashed lines in Fig. 1(b), and the local transformation strains close to the colony interfaces are not compatible. Therefore, the specific geometric combination of the martensite plate colony should result from the self-accommodation of elastic strains generated by the structural transformation (from austenite to martensite). Hereto, the martensitic transformation OR and the associated hierarchical martensite variant organization features of Ni 50 Mn 38 Sb 12 are fully detected, which will provide fundamental information for further investigation of property optimization of Ni-Mn-Sb intermetallic materials.

Summary
In this work, martensite variant organization features and the underlying formation mechanism in the Ni 50 Mn 38 Sb 12 intermetallic compound has been thoroughly investigated by SEM/ EBSD, the spatially correlated microstructure and crystallographic orientation analysis technique, and crystallographic calculations. The main results are as follows: (i) The martensite variants are hierarchically organized into plates and the plates into plate colonies. Each plate contains four distinct variants and each plate colony four distinct plates, with a total of 16 distinct variants.
(ii) The plates are separated by two kinds of plate interfaces, compatible and incompatible, depending on whether the interface plane is constituted of the common planes shared by the variants connected by the interface or not.
(iii) The martensitic transformation obeys the Pitsch OR specified as {011} A // {221} M and h011i A // h122i M . Such an OR results in a specific geometric configuration of the plate colonies. The four variants in each plate share one {011} A plane and the compatible plate interface corresponds to another {011} A plane. The three {011} A planes possessed by each pair of compatible plates, one corresponding to the compatible plate interface and the others to the four variants in each plate, are interrelated by 60 and belong to one h111i A axis zone. The characteristic {011} A planes of the two pairs of compatible plates in each plate colony belong to two h111i A axis zones having one {011} A plane in common. This common plane defines the compatible plate interfaces of the two pairs of plates as well as the plate colony. Hence, in theory, six distinct plate colonies should be produced in one original austenite, even though only three colonies were observed in this work.
(iv) The specific variant organization feature in this Ni-Mn-Sb alloy originates from the specific lattice deformation for the structure transformation. For compatible plates, the transformation strains for the formation of the variants are totally compatible at the plate interface, demonstrating an edge-toedge character. Thus, compatible plates should form and grow simultaneously. For the incompatible plates, the transformation strains at the plate interface are not compatible, so the interface should be formed when plates meet during the transformation process.
The results of the present work provide basic information for Ni-Mn-Sb intermetallic compounds and could be useful for interpreting their magnetic and mechanical characteristics associated with the martensitic transformation, and for further investigation of martensitic transformation crystallography of these materials.