Microstructural and In Situ Lorentz TEM Domain Characterization of As-Quenched and γ’-Precipitated Co49Ni30Ga21 Monocrystal

The article concerns the rarely described magnetic domain structure of Heusler alloys in the case of a single crystal [100]-oriented Co-Ni-Ga alloy. The structure of the magnetic domains of the alloy was compared in two states: in the quenched and additionally aged state. Ageing led to precipitation of the spherical phase γ’ nanoparticles (Co-rich, FCC lattice with a = 0.359 nm). Lorentz transmission electron microscopy observation methods combined with cooling and in situ heating of the sample in the transmission electron microscope in the temperature range from 140 K to 300 K were combined to observe the magnetic domain structure. Significant differences in the dimensions and morphology of magnetic domain boundaries have been demonstrated. The quenched sample showed no change in stripe domain structure when the aged sample showed significant development of branching magnetic structures. This may be due to a change in the chemical composition of the matrix resulting from a decrease in cobalt and nickel content at the expense of precipitations.


Introduction
Microstructure observations of magnetic shape memory alloys (MSMA) have always been a way to explain magnetic and physical phenomena [1]. However, before we discuss the magnetic structure of MSMA, we should briefly describe all the phases that may exist in scientifically popular alloys. The exact appearance of the binary graph of the Ni-Ga binary system has been investigated from the 1940s [2] and is still the subject of considerations [3]. The Co-Ni binary system comprises one phase: a substitutional solid solution with unlimited solubility. The Co-Ni binary alloys, which contain less than 30% of Ni, can undergo martensitic transformation close to room temperatures [4]. In the ternary Co-Ni-Ga system, there are three elements, which differ significantly in the shape of the crystal lattice. This causes that there are many intermetallic phases in the system. At room temperature, most of the tested Co-Ni-Ga alloys exhibit a stable one-phase or two-phase structure. The phase equilibria between the B2, γ, and γ' phases in the Co-Ni-Ga system and phase structures are rather similar to those in Co-Ni-Al because Al and Ga belong to the same group in the periodic table [5]. The B2 type, body-centred cubic austenite phase, with a lattice parameter a = 0.287 nm, was determined at room temperature [6,7]. The lattice parameters of the low-temperature martensite phase have been determined to be the L1 0 type tetragonal lattice with parameters a = 0.391 nm and c = 0.315 nm [8]. The layered martensitic structures, which were encountered frequently in Ni-Mn-Ga [9] and Ni-Fe-Ga alloys, have not been found in the Co-Ni-Ga system [5]. In addition, for the Co-Ni-Ga alloy, there was no tendency to additionally order the crystal lattice at high temperatures, as noted for the Ni-Mn-Ga alloy [10]. Most sources state that both the macroscopic and nanometric crystals of the γ' phase have a face-centred cubic lattice with a parameter a = 0.359 nm [11][12][13]. One of the teams, using the X-ray diffraction method, measured that the γ phase has a cubic structure with a parameter a = 0.408 nm [14]. It is common in the literature to describe the electron diffraction patterns characteristic of γ as the diffraction from the γ' phase [15]. Precipitation of the γ' phase causes a decrease in Ni concentration in the B2 phase matrix [5].
Soon after the discovery of the interesting properties of the one-phase Co-Ni-Ga alloy, it was discovered that it may be subjected to quenching and ageing in order to separate fine-dispersed precipitates of γ' phase from the austenite matrix. The particles gave characteristic, additional diffraction reflections and a clear image in the bright-and dark-field TEM observations [8]. Ageing treatments at 620 K performed in Co 49 Ni 21 Ga 30 single crystals have been found to generate dense dispersions of precipitates. These particles have a strong influence on the martensitic transformation, decreasing the overall transformation temperatures [16]. This is justified by the change in the chemical composition of the matrix: the B2 phase. It has also been proven that different temperatures and ageing times lead to separation and different shapes, from spherical to needle-like [17]. Variations in the size and morphology of precipitates have also been achieved by ageing under the additional effect of compressive stress [15]. A similar effect of precipitating was also observed for the Co-Ni-Al [18] and Fe-Ni-Co-Al-Ta [19] alloys.
In situ TEM heating experiments for the Co-Ni-Ga alloy were only performed for the Co 46 Ni 27 Ga 27 polycrystalline alloy [13]. The results confirmed a crystallographic relation between the austenitic, martensitic and γ phase: (111) L1 0 || (110) B2 || (111)γ. It has been shown that the martensite structure in Co-Ni-Ga alloys can present the multi-variant structure with a high amount of twinning [5]. From the selected area diffraction pattern there is a possibility to confirm the theoretically probable twinning habitus plane as (111) [11]. The Co-Ni-Ga quenched alloy exhibits a characteristic tweed pattern in the austenitic B2 phase [20]. In [21], the authors connected the tweed pattern with diffuse streaks along the {110} plane's family directions. The authors of [22] demonstrated observations of tweed with a high-resolution Lorentz transmission electron microscopy (TEM) microscope. It proved the dual, magnetic, and elastic nature of the tweed pattern. The phenomenon of tweed structure, however, has still not been fully explained. In the Ni-Fe-Ga system, it was observed that the presence of a tweed pattern is associated with the presence of additional, longitudinal electron diffraction spots [23]. TEM observations, combined with differential scanning calorimetry (DSC) measurements, allowed the tweed pattern to be assigned with the premartensitic transformation phenomena [24].
Studies on the domain structure of Co-Ni-Ga alloys can be divided due to observation methods: magnetic force microscopy (MFM), and light or electron microscopy. Light microscopy is still the most frequently used technique that allows many phenomena occurring in shape memory alloys to be described [25]. Observations of the Co 48 Ni 22 Ga 30 single crystal using polarized light microscopy, called Kerr microscopy, showed that in a martensitic state each martensitic plane is divided into 180 • magnetic domains and the twin boundaries are 90 • magnetic domain walls of the Bloch type [26]. The 180 • magnetic domains are continuous within the crystal grains and intersect the planar mutually parallel walls of the martensitic domains.
In situ observations during the interaction with the magnetic field allowed it to be stated that after the magnetization of the alloy, the new family of magnetic domains exhibits similar structural features as the original ones, but with the orientation characteristic of the applied magnetic field [27]. MFM gives the opportunity to observe structures on similar scales as TEM and were used to describe magnetic anisotropy [28][29][30][31]. MFM method in Co 45 Ni 25 Ga 30 alloy allowed to observe high magnetic anisotropy of the B2 phase [28]. However, the impact of crystal orientation on the domain structure of the alloy was not considered, so it is difficult to accurately refer to these results. Direct magnetic measurements determined that the {100} planes of the B2 phase coincide with the direction of easy magnetization of Co 47.5 Ni 22.5 Ga 30.0 single crystals [32].
Changes in the domain structure of magnetic shape memory materials as a function of temperature were not a frequent subject of research. The existence of magnetic domain wall contrast in the Co-Ni-Al alloy, whereas using the Lorentz TEM indicated that the sample is ferromagnetic at this temperature [18]. The alloy changed its magnetic structure at lower temperatures-magnetic domains in 219 K were 4 µm wide, and in 105 K were only 200 nm wide. The authors of [21] observed the domain structure of the Co 48 Ni 22 Ga 30 alloy in a quenched state, but only in the low-temperature martensite phase. They noticed parallel domains approximately 300 nm wide. A much more random shape of the magnetic domains was observed for the Ni-Mn-Ga alloy. At the same time, domain repeatability was recorded during subsequent in situ magnetic transformation cycles [33].
This work is an extension of the static domain structure observation published earlier [34]. The work [34] incorrectly uses the assumption that the Foucault method was used to observe the domain structure. Instead, it was observed using a specially developed method of revealing magnetic domains by means of ion polishing [35]. Due to the fact that the ion polishing method permanently and irreversibly reveals the magnetic structure, in this work, the Fresnel observation methods were used. The important value of this work is to examine the material in two different heat treatment states, as well as at temperatures in the range from 130 K to 300 K.

Materials and Methods
The Co 49 Ni 21 Ga 30 alloy of nominal weight composition was prepared from powders of Co, Ni, and Ga by melting in a high-frequency induction furnace under high vacuum conditions. The Co 49 Ni 21 Ga 30 alloy [001] oriented monocrystal was obtained using the modified Bridgman method, as in work [17,[36][37][38]. The crystal growing was performed on a modified REDMET-1 unit courtesy of Prof. Yuri Chumlaykov in Tomsk State University.
For maximum chemical homogeneity of single crystals, samples of Co 49 Ni 21 Ga 30 were then annealed at 1443 K for 8h in a quartz tube in a helium atmosphere, followed by quenching in water. It made the material into a metastable one-phase state. To obtain the presence of spherical, nanometric precipitates, some of the samples underwent an additional process of ageing at 603 K for 15 min.
The samples for TEM observations were prepared using mechanical thinning down to 100 µm, followed by electrolytic polishing using Struers Tenupol 5 and reagent containing 10% perchloric acid in butoxyethanol.
The microscope used in most of the work was a Hitachi H-800, equipped with a tungsten filament and an Olympus Quemesa camera. The operating voltage of the device was 150 kV. TEM observations of the magnetic structure were performed with the Fresnel method [39,40] using "free lens mode", which allows the operator to manually set the value of each current in the electron lenses. It allows the sample image to be focused using the first intermediate lens instead of the switched-off objective lens. Due to the stepping characteristics of the intermediate lens focusing, it was not always possible to determine the ideal in-focus position. In this case, the image with the weakest contrast coming from the magnetic structures was used for the in-focus image. Due to the fact that the only values controlled were the currents flowing through the lenses and sufficient information about the construction of the optical system was not provided, in most pictures we cannot specify the defocus value. The maximum magnetic field in the pole piece gap, with the objective lens switched off (residual magnetization of objective pole-piece), was measured using an Asonik SMS 102 hall probe magnetometer and amounted to 6 mT. In situ cooling experiments were performed using a side-entry cooling holder-a modified Hitachi H-5001C, with operating temperatures of 130~300 K, the T-type thermocouple and digital indication of temperature. The holder ensures an unchangeable heating/cooling rate, which is presented in Figure 1. The cooling rate determined for the holder was~20 K/min, and for heating was from 2 to 4 K/min. The device allows continuous and stable observations only at the temperature range of 130 K or 300 K. Fresnel imaging was performed during the continuous heating process, so the image sets at a given temperature were made with a discrepancy of~4 K. Selected area electron diffraction (SAED) patterns were calculated using DYFR software, originally created by Prof. Włodzimierz Dudziński in the Institute of Material Science and Mechanical Engineering at Wroclaw University of Science and Technology. The software has been used in a number of previous publications [41][42][43]. Calculations were taken by comparing the results of the diffractogram measurements with the database of all available patterns for probable phases.
Additional, static observation of the magnetic microstructure of the quenched Co49Ni21Ga30 sample was performed on a high-resolution JEOL JEM-F200 CR transmission microscope, using accelerating voltage of 200 kV. The Lorentz mode was available using Low-Mag function, with an objective lens turned off and objective mini-lens turned on. The residual magnetization of the objective pole-piece was not measured, so these results will only be considered as the direction of the next study.

Results
For both types of samples, after preliminary room temperature observations, a series of in situ experiments were performed in the TEM microscope column. Observations were made successively during continuous cooling of the sample to a temperature of ~130 K while being held at this temperature for 1 hour, and then during continuous, slow heating to ambient temperature. The experiment was repeated for three samples, and in the further part of the work, the results obtained during many separate experiments were summarized. The monocrystalline nature of the material does not allow the transformation mechanism to be clearly illustrated. Observation of structural changes is also difficult due to the non-diffusion nature of the martensitic transformation and deformation of the thin sample during cooling and heating. Samples due to undergoing a transformation in a limited volume of thin foil cracked and did not allow observations during more than 2−3 cooling cycles.

Co49Ni21Ga30 in the Quenched State
The microstructure of the Co49Ni21Ga30 monocrystal in its quenched state was observed in the austenite phase [001] zone axis. Bright-field imaging mainly revealed the contrast associated with the presence of extinction contours. However, the course of the line indicates the presence of disturbances in the crystal structure, probably slip bands (Figure 2a). No dislocation or twinning structure was observed, which corresponds well with the heat treatment consisting of annealing for 8 hours and quenching in water. Selected area diffraction patterns taken from non-tilted samples clearly show the presence of diffractions spots, which can be attributed to the B2 body-centred cubic lattice. The orientation of the crystal on the direction [001] was confirmed (Figure 2b). Selected area electron diffraction (SAED) patterns were calculated using DYFR software, originally created by Prof. Włodzimierz Dudziński in the Institute of Material Science and Mechanical Engineering at Wroclaw University of Science and Technology. The software has been used in a number of previous publications [41][42][43]. Calculations were taken by comparing the results of the diffractogram measurements with the database of all available patterns for probable phases.
Additional, static observation of the magnetic microstructure of the quenched Co 49 Ni 21 Ga 30 sample was performed on a high-resolution JEOL JEM-F200 CR transmission microscope, using accelerating voltage of 200 kV. The Lorentz mode was available using Low-Mag function, with an objective lens turned off and objective mini-lens turned on. The residual magnetization of the objective pole-piece was not measured, so these results will only be considered as the direction of the next study.

Results
For both types of samples, after preliminary room temperature observations, a series of in situ experiments were performed in the TEM microscope column. Observations were made successively during continuous cooling of the sample to a temperature of~130 K while being held at this temperature for 1 h, and then during continuous, slow heating to ambient temperature. The experiment was repeated for three samples, and in the further part of the work, the results obtained during many separate experiments were summarized. The monocrystalline nature of the material does not allow the transformation mechanism to be clearly illustrated. Observation of structural changes is also difficult due to the non-diffusion nature of the martensitic transformation and deformation of the thin sample during cooling and heating. Samples due to undergoing a transformation in a limited volume of thin foil cracked and did not allow observations during more than 2-3 cooling cycles.

Co 49 Ni 21 Ga 30 in the Quenched State
The microstructure of the Co 49 Ni 21 Ga 30 monocrystal in its quenched state was observed in the austenite phase [001] zone axis. Bright-field imaging mainly revealed the contrast associated with the presence of extinction contours. However, the course of the line indicates the presence of disturbances in the crystal structure, probably slip bands ( Figure 2a). No dislocation or twinning structure was observed, which corresponds well with the heat treatment consisting of annealing for 8 h and quenching in water. Selected area diffraction patterns taken from non-tilted samples clearly show the presence of diffractions spots, which can be attributed to the B2 body-centred cubic lattice. The orientation of the crystal on the direction [001] was confirmed ( Figure 2b). Some diffractograms showed the elongation and blurring of some diffraction points to the inside or outside of the pattern (Figure 2b). According to literature data, a similar phenomenon may be justified in the case of hard magnetic materials with a noticeable domain structure [44][45][46]. The effects related to the magnetic structure of the sample and diffraction patterns have been described more detail in the paper [34]. Therefore, areas characterized by such diffraction patterns were subjected to Fresnel domain observations. An exemplary set of images in the under-focus, in-focus, and overfocus images are presented in Figure 3a. The under-and over-focus positions show the inverse contrast of vertical bands, which indicates the magnetic nature of the image.
The magnetic domain structure of the Co49Ni21Ga30 monocrystal in its quenched state consists of ~150nm width parallel magnetic domains, arranged along the {001} austenite phase planes. At the same time, micrometric, rhomboidal domains were observed, e.g., below the frame mark in Figure  3a. The coexistence of both types of domains (microscopic and highly periodic stripe domains) may be due to local heterogeneity in the magnetic properties of the material or local magnetic orientation along different planes of the {100} family. Under-and over-focused images were subtracted from each other, which allowed better visualization of the contrast of magnetic domain boundaries ( Figure 3b).  Some diffractograms showed the elongation and blurring of some diffraction points to the inside or outside of the pattern (Figure 2b). According to literature data, a similar phenomenon may be justified in the case of hard magnetic materials with a noticeable domain structure [44][45][46]. The effects related to the magnetic structure of the sample and diffraction patterns have been described more detail in the paper [34]. Therefore, areas characterized by such diffraction patterns were subjected to Fresnel domain observations. An exemplary set of images in the under-focus, in-focus, and over-focus images are presented in Figure 3a. The under-and over-focus positions show the inverse contrast of vertical bands, which indicates the magnetic nature of the image. Some diffractograms showed the elongation and blurring of some diffraction points to the inside or outside of the pattern (Figure 2b). According to literature data, a similar phenomenon may be justified in the case of hard magnetic materials with a noticeable domain structure [44][45][46]. The effects related to the magnetic structure of the sample and diffraction patterns have been described more detail in the paper [34]. Therefore, areas characterized by such diffraction patterns were subjected to Fresnel domain observations. An exemplary set of images in the under-focus, in-focus, and overfocus images are presented in Figure 3a. The under-and over-focus positions show the inverse contrast of vertical bands, which indicates the magnetic nature of the image.
The magnetic domain structure of the Co49Ni21Ga30 monocrystal in its quenched state consists of ~150nm width parallel magnetic domains, arranged along the {001} austenite phase planes. At the same time, micrometric, rhomboidal domains were observed, e.g., below the frame mark in Figure  3a. The coexistence of both types of domains (microscopic and highly periodic stripe domains) may be due to local heterogeneity in the magnetic properties of the material or local magnetic orientation along different planes of the {100} family. Under-and over-focused images were subtracted from each other, which allowed better visualization of the contrast of magnetic domain boundaries (Figure 3b).  The magnetic domain structure of the Co 49 Ni 21 Ga 30 monocrystal in its quenched state consists of 150 nm width parallel magnetic domains, arranged along the {001} austenite phase planes. At the same time, micrometric, rhomboidal domains were observed, e.g., below the frame mark in Figure 3a. The coexistence of both types of domains (microscopic and highly periodic stripe domains) may be due to local heterogeneity in the magnetic properties of the material or local magnetic orientation along different planes of the {100} family. Under-and over-focused images were subtracted from each other, which allowed better visualization of the contrast of magnetic domain boundaries (Figure 3b).
Prior to the cooling process of one of the samples, it was rotated to receive the [011] zone axis of B2 austenite diffraction pattern at 293 K (Figure 4a). Additional diffraction points were visible, and identical to those observable in Figure 2b. Diffusion streaks were also observed, which may suggest the presence of a long-term ordering of the structure. Immediately after the transformation, the observed place bent, which at temperatures of 220~250 K made it difficult to obtain the correct diffraction pattern without changing the tilt angle (Figure 4b,c). Only at 152 K and lower temperatures, it was possible to obtain the elementary cell associated with the L1 0 network of the martensitic phase in Figure 4d. The SAED taken from the martensite phase also reveal the presence of doubled spots, which can be caused by an internal strong magnetic field related to domain structure (marked in Figure 4d). Prior to the cooling process of one of the samples, it was rotated to receive the [01 � 1] zone axis of B2 austenite diffraction pattern at 293 K (Figure 4a). Additional diffraction points were visible, and identical to those observable in Figure 2b. Diffusion streaks were also observed, which may suggest the presence of a long-term ordering of the structure. Immediately after the transformation, the observed place bent, which at temperatures of 220~250 K made it difficult to obtain the correct diffraction pattern without changing the tilt angle (Figure 4b, c). Only at 152 K and lower temperatures, it was possible to obtain the elementary cell associated with the L10 network of the martensitic phase in Figure 4d. The SAED taken from the martensite phase also reveal the presence of doubled spots, which can be caused by an internal strong magnetic field related to domain structure (marked in Figure 4d). As similar effects on electron diffraction were observed for both the martensitic and austenitic phases, it was decided to compare the domain structure of the alloy in situ during the cooling process. Preliminary observations showed that the domain structure does not change significantly, and therefore Figure 5 shows the Fresnel images obtained at different temperatures. At lower temperatures, a significant change in the geometry of the thin film and the appearance of new extinction contours are clearly visible. However, in the magnetic domains marked with the frame, there were no significant changes and it still showed the presence of parallel domains of ~150 nm in width. To objectively compare the contrast in the out of focus positions, the under-focus images were subtracted from the over-focus images. This process was performed for three sets of images. The first is the material before in situ cooling, the second is the sample cooled to 143 K, and in the third, the material was heated back to ambient temperature. Analysis of the processed images indicated that during cooling and heating there may exist a slight reconstruction of the domain structure, but its accurate tracking requires a resolution of the order of single nanometers, which is impossible to obtain with the current configuration of the used device. However, in the entire range of As similar effects on electron diffraction were observed for both the martensitic and austenitic phases, it was decided to compare the domain structure of the alloy in situ during the cooling process. Preliminary observations showed that the domain structure does not change significantly, and therefore Figure 5 shows the Fresnel images obtained at different temperatures. At lower temperatures, a significant change in the geometry of the thin film and the appearance of new extinction contours are clearly visible. However, in the magnetic domains marked with the frame, there were no significant changes and it still showed the presence of parallel domains of~150 nm in width. To objectively compare the contrast in the out of focus positions, the under-focus images were subtracted from the over-focus images. This process was performed for three sets of images. The first is the material before in situ cooling, the second is the sample cooled to 143 K, and in the third, the material was heated back to ambient temperature. Analysis of the processed images indicated that during cooling and heating there may exist a slight reconstruction of the domain structure, but its accurate tracking requires a resolution of the order of single nanometers, which is impossible to obtain with the current configuration of the used device. However, in the entire range of temperatures, the tested visible domains have a parallel orientation and width from 100 to 200 nm, without any significant changes ( Figure 6). temperatures, the tested visible domains have a parallel orientation and width from 100 to 200 nm, without any significant changes ( Figure 6).  To check further observation perspectives using more resolved electron microscopes, additional observations were performed using a JEOL JEM-F200 CR microscope. The microscope has a standard, implemented solution for observation using Fresnel methods, so we managed to determine the defocus amount for under-and over-focus at 18 µm. In addition to confirming previous observations, internal magnetic subdomains of up to 12 nm have been observed (Figure 7). Determining the magnetic structure as a function of temperature using more advanced microscopes than the previously used Hitachi H-800 and comparing all results is a promising direction for further research. temperatures, the tested visible domains have a parallel orientation and width from 100 to 200 nm, without any significant changes ( Figure 6).  To check further observation perspectives using more resolved electron microscopes, additional observations were performed using a JEOL JEM-F200 CR microscope. The microscope has a standard, implemented solution for observation using Fresnel methods, so we managed to determine the defocus amount for under-and over-focus at 18 µm. In addition to confirming previous observations, internal magnetic subdomains of up to 12 nm have been observed (Figure 7). Determining the magnetic structure as a function of temperature using more advanced microscopes than the previously used Hitachi H-800 and comparing all results is a promising direction for further research. To check further observation perspectives using more resolved electron microscopes, additional observations were performed using a JEOL JEM-F200 CR microscope. The microscope has a standard, implemented solution for observation using Fresnel methods, so we managed to determine the defocus amount for under-and over-focus at 18 µm. In addition to confirming previous observations, internal magnetic subdomains of up to 12 nm have been observed (Figure 7). Determining the magnetic structure as a function of temperature using more advanced microscopes than the previously used Hitachi H-800 and comparing all results is a promising direction for further research.

Co49Ni21Ga30 in the Quenched and Aged State
The microstructure of the Co49Ni21Ga30 monocrystal in its quenched and aged state was observed in the austenite phase [001] zone axis. Bright-field imaging revealed no extinction contours and the presence of a significant number of spherical γ' precipitates. A large number of precipitates made it very difficult to observe the structural effects associated with the B2 austenite matrix (Figure 8a,b). Locally, places with a lower density of precipitates can be observed along the planes (011) and (200) (Figure 8b, c). Their presence may be related to the more difficult release of particles during ageing near defects such as slip or twins, which was observed previously in the quenched sample.

Co 49 Ni 21 Ga 30 in the Quenched and Aged State
The microstructure of the Co 49 Ni 21 Ga 30 monocrystal in its quenched and aged state was observed in the austenite phase [001] zone axis. Bright-field imaging revealed no extinction contours and the presence of a significant number of spherical γ' precipitates. A large number of precipitates made it very difficult to observe the structural effects associated with the B2 austenite matrix (Figure 8a,b). Locally, places with a lower density of precipitates can be observed along the planes (011) and (200) (Figure 8b,c). Their presence may be related to the more difficult release of particles during ageing near defects such as slip or twins, which was observed previously in the quenched sample.

Co49Ni21Ga30 in the Quenched and Aged State
The microstructure of the Co49Ni21Ga30 monocrystal in its quenched and aged state was observed in the austenite phase [001] zone axis. Bright-field imaging revealed no extinction contours and the presence of a significant number of spherical γ' precipitates. A large number of precipitates made it very difficult to observe the structural effects associated with the B2 austenite matrix (Figure 8a,b). Locally, places with a lower density of precipitates can be observed along the planes (011) and (200) (Figure 8b, c). Their presence may be related to the more difficult release of particles during ageing near defects such as slip or twins, which was observed previously in the quenched sample.  in the [100] zone axis allowed additional spots to be recognized as γ' phase (Co-rich, FCC lattice with a = 0.359 nm) precipitations (Figure 9b). Unlike the quenched sample, it is not possible to obtain a diffraction pattern without the additional diffractions spots. The presence of γ' precipitations was finally confirmed by TEM observations in the dark field. The images obtained using the bright-and dark-field methods were data allowing precise determination of the size and shapes of the nanoparticles using image processing software. After thresholding, using a semi-automatic script in the ImageJ program [47], each particle was approximated as an ellipse, and the transversal and conjugate diameter was measured. The particle size was expressed as the mean of these two diameters, and for the tested material it was 12.9 nm with a standard deviation of 2.4 nm (Figure 10). Fresnel imaging of the Co49Ni21Ga30 monocrystal in its quenched and aged state was performed with the objective lens switched off. An exemplary set of images in the under-focus, in-focus and over-focus positions is presented in Figure 11. The under-and over-focus positions show no contrast connected with the magnetic properties of the material at the temperature of 293 K. The images obtained using the bright-and dark-field methods were data allowing precise determination of the size and shapes of the nanoparticles using image processing software. After thresholding, using a semi-automatic script in the ImageJ program [47], each particle was approximated as an ellipse, and the transversal and conjugate diameter was measured. The particle size was expressed as the mean of these two diameters, and for the tested material it was 12.9 nm with a standard deviation of 2.4 nm (Figure 10). in the [100] zone axis allowed additional spots to be recognized as γ' phase (Co-rich, FCC lattice with a = 0.359 nm) precipitations (Figure 9b). Unlike the quenched sample, it is not possible to obtain a diffraction pattern without the additional diffractions spots. The presence of γ' precipitations was finally confirmed by TEM observations in the dark field. The images obtained using the bright-and dark-field methods were data allowing precise determination of the size and shapes of the nanoparticles using image processing software. After thresholding, using a semi-automatic script in the ImageJ program [47], each particle was approximated as an ellipse, and the transversal and conjugate diameter was measured. The particle size was expressed as the mean of these two diameters, and for the tested material it was 12.9 nm with a standard deviation of 2.4 nm (Figure 10). Fresnel imaging of the Co49Ni21Ga30 monocrystal in its quenched and aged state was performed with the objective lens switched off. An exemplary set of images in the under-focus, in-focus and over-focus positions is presented in Figure 11. The under-and over-focus positions show no contrast connected with the magnetic properties of the material at the temperature of 293 K. Fresnel imaging of the Co 49 Ni 21 Ga 30 monocrystal in its quenched and aged state was performed with the objective lens switched off. An exemplary set of images in the under-focus, in-focus and over-focus positions is presented in Figure 11. The under-and over-focus positions show no contrast connected with the magnetic properties of the material at the temperature of 293 K.  A significant difference in the domain structure at ambient temperature and cooled state caused the need to observe the change in the domain structure as a function of temperature. A series of observations were made during the continuous heating of the sample. Due to the impossibility of stopping the heating process, observations at each temperature were made as quickly as possible. Therefore, temperature discrepancies during observations should not exceed ± 2 K. For the best photo sets, subtractions of under-and over-focus images were taken to obtain a clean image of the domain boundaries. The development of the domain structure at temperatures of 273 K, 233 K, and 143 K is presented in Figure 13. Magnetic domains are not visible at 273 K, slightly revealed at 233 K, and clearly noticeable at 143 K. Extensive set of the Fresnel images was added in Appendix A. The difference between under-and over-focus images is not an image of domains, but only an image of one family of domain borders (white or black). This is a method that is convenient for revealing stripe  A significant difference in the domain structure at ambient temperature and cooled state caused the need to observe the change in the domain structure as a function of temperature. A series of observations were made during the continuous heating of the sample. Due to the impossibility of stopping the heating process, observations at each temperature were made as quickly as possible. Therefore, temperature discrepancies during observations should not exceed ± 2 K. For the best photo sets, subtractions of under-and over-focus images were taken to obtain a clean image of the domain boundaries. The development of the domain structure at temperatures of 273 K, 233 K, and 143 K is presented in Figure 13. Magnetic domains are not visible at 273 K, slightly revealed at 233 K, and clearly noticeable at 143 K. Extensive set of the Fresnel images was added in Appendix A. The difference between under-and over-focus images is not an image of domains, but only an image of one family of domain borders (white or black). This is a method that is convenient for revealing stripe A significant difference in the domain structure at ambient temperature and cooled state caused the need to observe the change in the domain structure as a function of temperature. A series of observations were made during the continuous heating of the sample. Due to the impossibility of stopping the heating process, observations at each temperature were made as quickly as possible. Therefore, temperature discrepancies during observations should not exceed ± 2 K. For the best photo sets, subtractions of under-and over-focus images were taken to obtain a clean image of the domain boundaries. The development of the domain structure at temperatures of 273 K, 233 K, and 143 K is presented in Figure 13. Magnetic domains are not visible at 273 K, slightly revealed at 233 K, and clearly noticeable at 143 K. Extensive set of the Fresnel images was added in Appendix A. The difference between under-and over-focus images is not an image of domains, but only an image of one family of domain borders (white or black). This is a method that is convenient for revealing stripe domains, and faulty for domains of a different shape. The exact shape of the branching domains, arranged in pairs parallel to each other, can be seen in Appendix A.  In situ bright-field microstructure analysis taken at 133 K reveals the presence of the structural defects. The dominating observable structure is internal twinning, both on a micro- (Figure 14a) and nanoscale (Figure 14b). There are no signs of internal slip, and twins often arrange themselves into multiscale structures: subgrains that have already been twinned can twin along different planes (Figure 14a, arrows). The presence of fine γ' precipitations do not affect the twinning inside the martensite matrix. Nanometric size martensite twins are formed with no observable interference between the martensite matrix ( Figure 15). Partial overlapping of nanoparticle and twins images can be explained by the fact that they exhibit partial coherence, and therefore also overlapping diffraction reflections. In situ bright-field microstructure analysis taken at 133 K reveals the presence of the structural defects. The dominating observable structure is internal twinning, both on a micro- (Figure 14a) and nanoscale (Figure 14b). There are no signs of internal slip, and twins often arrange themselves into multiscale structures: subgrains that have already been twinned can twin along different planes (Figure 14a, arrows).  In situ bright-field microstructure analysis taken at 133 K reveals the presence of the structural defects. The dominating observable structure is internal twinning, both on a micro-( Figure 14a) and nanoscale (Figure 14b). There are no signs of internal slip, and twins often arrange themselves into multiscale structures: subgrains that have already been twinned can twin along different planes (Figure 14a, arrows). The presence of fine γ' precipitations do not affect the twinning inside the martensite matrix. Nanometric size martensite twins are formed with no observable interference between the martensite matrix ( Figure 15). Partial overlapping of nanoparticle and twins images can be explained by the fact that they exhibit partial coherence, and therefore also overlapping diffraction reflections. The presence of fine γ' precipitations do not affect the twinning inside the martensite matrix. Nanometric size martensite twins are formed with no observable interference between the martensite matrix ( Figure 15). Partial overlapping of nanoparticle and twins images can be explained by the fact that they exhibit partial coherence, and therefore also overlapping diffraction reflections.

Discussion
Room temperature observations of the Co49Ni21Ga30 [001]-oriented single crystal in its quenched state by means of TEM methods allowed to observe a homogeneous, single-phase microstructure of B2 austenite with slip occurred on the {001} plane family (Figure 2a). Room temperature observations of the Co49Ni21Ga30 [001]-oriented single crystal in its quenched and aged state did not show the presence of a tweed pattern, but most of the field of view was covered with γ' nanoparticles ( Figure  8) of the size 12,9 ± 2,4 nm ( Figure 9). The presence of the γ' phase, sometimes misinterpreted as the ω phase, was confirmed by diffraction patterns taken in a different zone axis (Figure 8). The size and slightly elongated spherical shape of the nanoparticles correspond to assumptions based on earlier work [17].
The martensite micro modulation found in [15] was not observed. There is a possibility that the authors described "micro modulation" for the presence of fine, nanometric twinning ( Figure 14). This theory has confirmation in high-resolution TEM (HRTEM) observations [15]. The authors of cited work additionally combine the presence of additional diffraction points with the presence of a special order inside the martensite structure. Observations described in the present research do not support this theory. The same paper makes the hypothesis of the presence of residual austenite in the martensitic material after quenching and ageing. The theory, however, did not receive full support in either work [25] or in the research described above.
Observations of the electron diffraction patterns of both sets of samples confirmed the presence of B2 to L10 transformations. Some of the SAED patterns of the quenched samples show the presence of similar additional diffraction spots as the spots corresponding to the presence of γ' coherent precipitations ( Figure 2; Figure 4). Their presence may be caused by the appearance of particles of a size that goes beyond the observation possibilities or local ordering of the crystal lattice. The second explanation corresponds to work [48], in which the authors show the possibility of making the Co-Ni-Ga alloy with additional local ordering.
The authors of this work performed imaging of the domain structure of the Co-Ni-Ga alloy during in situ TEM heating at temperatures of 140-300 K. The magnetic domain observations by means of Fresnel TEM imaging did not show the presence of a cross-tie wall (comparable to work in [49]), but instead of Neel or Bloch domain walls. The distinction between the two possible types of domain boundaries was not possible with the available observation method. The material in the quenched state showed no major changes in the orientation of its magnetic structure at the temperatures of 140 K to 300 K ( Figure 6). It showed the presence of almost parallel, elongated domains with a width of 100-200 nm and oriented along {001} plane family. This agrees with literature data according to which the (100) planes of the B2 phase coincide with the direction of easy magnetization of Co-Ni-Ga single crystals [32]. This agrees with the results of previous studies, where on two sides of the thin foil two families of magnetic domains were observed, oriented towards each other at an angle of 90 * and parallel to the {001} plane family of B2 phase [35]. At the same time, this differs from observations carried out on Ni-Mn-Ga alloys, where domains arranged along (110) Figure 15. Dark-field TEM images of (a) the twinned martensite phase and (b) γ' nanoparticles at the temperature of 133 K.

Discussion
Room temperature observations of the Co 49 Ni 21 Ga 30 [001]-oriented single crystal in its quenched state by means of TEM methods allowed to observe a homogeneous, single-phase microstructure of B2 austenite with slip occurred on the {001} plane family (Figure 2a). Room temperature observations of the Co 49 Ni 21 Ga 30 [001]-oriented single crystal in its quenched and aged state did not show the presence of a tweed pattern, but most of the field of view was covered with γ' nanoparticles ( Figure 8) of the size 12.9 ± 2.4 nm (Figure 9). The presence of the γ' phase, sometimes misinterpreted as the ω phase, was confirmed by diffraction patterns taken in a different zone axis (Figure 8). The size and slightly elongated spherical shape of the nanoparticles correspond to assumptions based on earlier work [17].
The martensite micro modulation found in [15] was not observed. There is a possibility that the authors described "micro modulation" for the presence of fine, nanometric twinning ( Figure 14). This theory has confirmation in high-resolution TEM (HRTEM) observations [15]. The authors of cited work additionally combine the presence of additional diffraction points with the presence of a special order inside the martensite structure. Observations described in the present research do not support this theory. The same paper makes the hypothesis of the presence of residual austenite in the martensitic material after quenching and ageing. The theory, however, did not receive full support in either work [25] or in the research described above.
Observations of the electron diffraction patterns of both sets of samples confirmed the presence of B2 to L1 0 transformations. Some of the SAED patterns of the quenched samples show the presence of similar additional diffraction spots as the spots corresponding to the presence of γ' coherent precipitations (Figures 2 and 4). Their presence may be caused by the appearance of particles of a size that goes beyond the observation possibilities or local ordering of the crystal lattice. The second explanation corresponds to work [48], in which the authors show the possibility of making the Co-Ni-Ga alloy with additional local ordering.
The authors of this work performed imaging of the domain structure of the Co-Ni-Ga alloy during in situ TEM heating at temperatures of 140-300 K. The magnetic domain observations by means of Fresnel TEM imaging did not show the presence of a cross-tie wall (comparable to work in [49]), but instead of Neel or Bloch domain walls. The distinction between the two possible types of domain boundaries was not possible with the available observation method. The material in the quenched state showed no major changes in the orientation of its magnetic structure at the temperatures of 140 K to 300 K ( Figure 6). It showed the presence of almost parallel, elongated domains with a width of 100-200 nm and oriented along {001} plane family. This agrees with literature data according to which the (100) planes of the B2 phase coincide with the direction of easy magnetization of Co-Ni-Ga single crystals [32]. This agrees with the results of previous studies, where on two sides of the thin foil two families of magnetic domains were observed, oriented towards each other at an angle of 90 * and parallel to the {001} plane family of B2 phase [35]. At the same time, this differs from observations carried out on Ni-Mn-Ga alloys, where domains arranged along (110) planes were observed [31]. The material in its quenched and aged state did not show the presence of any magnetic domain wall at room temperature ( Figure 10), but when lowering the temperature, it showed a growing contrast from the domain walls ( Figure 11). The material in its quenched and aged state at 140 K presented an irregular arranged domain with a size of up to 1 µm (Figures 11 and 12). Note that the in situ observation of the development of the magnetic domain structure in the shape memory material at reduced temperatures was rarely mentioned in the literature [18].
Comparison of literature [50] with the domain images contained in the practical part of the work allows the domains of material in its quenched state to be characterized as stripe domains with a minimal amount of branching, which are especially visible in Figure 3. The Co 49 Ni 21 Ga 30 crystal in its quenched and aged state shows a domain structure with clearly influenced branching ( Figure 12).
The domain structure of the Co 49 Ni 21 Ga 30 single crystal in the [100] zone axis presents some similarities to that obtained for the magnetostrictive material during annealing with the additional influence of a magnetic field. In [50], the induced magnetic anisotropy with the easy axis perpendicular to the sample surface was produced. In the case of the author's own research, the orientation of domains was very similar, but it arose spontaneously, or under the influence of random disturbances from the environment. We hope that the observations of the domain structure development will help justify the mechanical differences between Co-Ni-Ga alloys after quenching and additional ageing [36,51].
The observations performed on high-resolution Lorentz TEM allowed us to observe fine, 12 nm wide, parallel magnetic domain boundaries in the quenched sample. They showed contrast many times weaker than the domain boundaries observed at conventional TEM, which may, however, depend on the defocus value not known in every microscope. One of the further research steps may therefore be the analysis of domain structure on various observational scales, from Kerr light microscopy, through low-resolution conventional TEM to state-of-the-art electron holography, MFM, or high-resolution Fresnel microscopy. It seems interesting to compare the results of the above work with an experiment carried out with the help of MFM methods [29,30], which, however, were used for in situ research [31]. Funding: This research received no external funding. Hannover (Federal Republic of Germany) for providing the research material and consultation. The authors would also thank Yu. I. Chumlyakov from State University Tomsk (Russian Federation) for producing single crystals, Aleksandra Królicka from Wroclaw University of Science and Technology (Poland) for helping in observation using the cooling/heating Lorentz TEM method, and for JEOL EUROPE for providing access for the high-resolution microscope.

Conflicts of Interest:
The authors declare no conflicts of interest.

Appendix A
Fresnel image sets for Co 49 Ni 21 Ga 30 monocrystal in its quenched and aged state at various intermediate temperatures are shown in Figures A1 and A2. In addition to the appearance of the domain structure, extinction contours can be seen moving, which is of course associated with a slight change in the shape and orientation of the sample during temperature change. It is worth remembering that the observations were made during the heating of the sample, and therefore the sample had a martensitic structure up to the temperature of 293 K.