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Eiichi Sei, Ken-ichi Ikeda, Seiji Miura, [Koji Morita](https://orcid.org/0000-0001-6040-7054), [Tohru S. Suzuki](https://orcid.org/0000-0001-9458-6863), [Yoshio Sakka](https://orcid.org/0000-0001-8357-5843)

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[Effect of Porosity on High Temperature Compressive Behavior of Textured Ti<sub>3</sub>SiC<sub>2</sub> Bodies Prepared by Pressureless Sintering](https://mdr.nims.go.jp/datasets/5334aff7-935b-420d-b6a2-41cea1e46b7d)

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Effect of Porosity on High Temperature Compressive Behavior of Textured Ti3SiC2 Bodies Prepared by Pressureless SinteringEffect of Porosity on High Temperature Compressive Behavior of Textured Ti3SiC2Bodies Prepared by Pressureless Sintering+1Eiichi Sei1,+2, Ken-ichi Ikeda2,+3, Seiji Miura2, Koji Morita3, Tohru S. Suzuki3 and Yoshio Sakka31Division of Materials Science and Engineering, Graduate School of Engineering, Hokkaido University, Sapporo 060-8628, Japan2Division of Materials Science and Engineering, Faculty of Engineering, Hokkaido University, Sapporo 060-8628, Japan3National Institute for Materials Science, Tsukuba 305-0047, JapanTo clarify the effect of pores on high temperature compressive behavior due to kink deformation, textured Ti3SiC2 pressureless sinteredbodies were fabricated and examined by high temperature compression tests with different porosities.The textured Ti3SiC2 pressureless sintered bodies were prepared by slip casting in a strong magnetic field and spark plasma sintering at1400°C for 1 h. Samples were cut into rectangular shape with 45° between the casting direction and the compression axis, and compression testswere conducted at 1200°C at a strain rate of 3 © 10¹4 s¹1. Porosity was evaluated by Archimedes method and binarization. Crystal orientationanalysis using EBSD method was performed to observe the microstructure evolution before and after the compression test.The sintered bodies had a strongly textured microstructure with homogeneous dispersed pores. The results of high temperaturecompression tests showed that the 0.2% proof stress depended on the porosity before compression tests. On the other hand, the work hardeningcoefficient was larger for plessureless sintered sample with high porosity, which attributed to the densification associated with the compression.Microstructural observations indicated that fine kink bands formed in the middle stage of the compression and then disappeared, suggesting thatthis is important for clarifying kink-band strengthening in the MAX phase. [doi:10.2320/matertrans.MT-M2025063](Received April 22, 2025; Accepted May 15, 2025; Published July 25, 2025)Keywords: Ti3SiC2, kink deformation, texture, porosity, high temperature deformation1. IntroductionMAX phases are ternary compounds with the generalformula Mn+1AXn (M: early transition metal, A: A-groupelement, X: C or N, n = 1–3). They are unique materialswith metallic (high thermal/electrical conductivity andmachinability) and ceramic (low density, high rigidity, andoxidation resistance) properties [1–3]. Ti3SiC2 is one of themost extensively studied MAX phases; it has a hexagonallayered crystal structure (a = 0.3067mm, c = 1.767mm) [1],in which Ti-C and Si layers are stacked along the c-axis.Therefore, it exhibits anisotropic properties [4–6] and basalslips as the predominant plastic deformation mechanism.Kink deformation is one of the deformation mechanisms inlayered materials. It has been confirmed in Cd [7], Zn [8],graphite [9], mica [10], polymers [11], and MAX phases[12–16]. Barsoum and El-Raghy [13] demonstrated thatkink deformation occurred in textured Ti3SiC2 when thecompression axis was perpendicular to the c-axis. Shirakamiet al. [6] have also performed compression tests on texturedTi3SiC2 at 1200°C and found that kink deformation was morepronounced when the angle between the compression axisand c-axis was 90° than when it was 0° or 45°. In addition,Matsui et al. [14, 15] evaluated the microstructure of Ti3SiC2polycrystals after high temperature compressive creep testsand reported that kink deformation occurred more frequentlyin grains whose orientation differed from the compressionaxis to the basal planes by within 10°. In contrast, Higashiet al. [16] have reported that kink deformation in Ti3SiC2single crystals occurs only when the compression direction isperpendicular to the c-axis (½�12�10� or ½�1100�), as shown byroom temperature micropillar compression tests.Kink-band strengthening has recently been proposed as anew strengthening mechanism, because kink bands, whichare deformation bands formed by kink deformation, act asobstacles to dislocation motion. This was first reported inMg-Zn-Y alloys with a long-period stacking ordered (LPSO)structure. For Mg alloys, Kawamura et al. [17, 18] performedtensile tests on specimens with kink bands introduced byhot extrusion and found that mechanical strength (e.g., 0.2%proof stress) improved via the kink-band strengthening.Somekawa et al. [19] concluded that kink boundaries withangles of 20° or more hinder dislocation motion. Kinkdeformation and kink-band strengthening at room temper-ature have also been confirmed in Al-Cu eutectic alloys [20].Although kink-band strengthening has been observed inMg/LPSO and Al-Cu alloys, it remains scarce in the MAXphases. One reason is that delamination, as well as theresidual pores formed during sintering, significantly affectsthe mechanical properties. Hashimoto et al. [21, 22] inves-tigated the effects of grain restriction on kink deformation byperforming high temperature compression tests on texturedTi3SiC2 dense and porous samples. They found that a weakerconstraint promoted more crystal rotation. The porous samplehad a porosity difference of approximately 10 vol%. There-fore, to understand the strengthening mechanism of Ti3SiC2,it is necessary to fabricate samples with uniformly dispersedpores and to investigate the relationships among mechanicalproperties, porosity, and kink deformation bands.As mentioned preciously, the relationship between thecrystallographic orientation and compression direction iscrucial for kink deformation. Therefore, alignment controlsimplifies the observation of kink deformation behavior [6,21, 22]. Tape-casting [23] and hot-pressing [24] are commontexturing techniques for ceramics; however, it is difficult+1This Paper was Originally Published in Japanese in J. Japan Inst. Met.Mater. 88 (2024) 297–305.+2Graduate Student, Hokkaido University+3Corresponding author, E-mail: ikeda.ken-ichi@eng.hokudai.ac.jpMaterials Transactions, Vol. 66, No. 8 (2025) pp. 1006 to 1013©2025 The Japan Institute of Metals and Materialshttps://doi.org/10.2320/matertrans.MT-M2025063to control the shape of the compacts and their orientationdirection. Therefore, slip casting in a strong magnetic field(SCMF) [25, 26] was conducted. Slip casting is a process inwhich raw powder is mixed with a liquid to prepare a slurry,which is then poured into a porous mold to remove thesolvent. Textured Ti3SiC2 was obtained through SCMF at12T [4–6, 21, 22, 27–29].This research has two objectives. The first is to fabricatetextured Ti3SiC2 with uniformly dispersed pores and toevaluate its microstructure. The second is to investigate howhigh temperature compressive behavior, porosity, and micro-structure are related to kink deformation.2. Experimental Procedures2.1 Slurry preparationFirst, commercial Ti3SiC2 powder (Maxthal (312),KANTHAL, particle size: 1–10 µm) was mixed with ethanolas a solvent, maintaining a powder content of 30 vol%.Polyethyleneimine (PEI, FUJIFILM Wako Pure ChemicalCorp.) was then added as a dispersant to prevent powderagglomeration in the slurry. The PEI content was 1.5mass%relative to the Ti3SiC2 powder. The slurry was redispersedusing an ultrasonic homogenizer (GSD-600AT, SonicTechnology Inc.) while stirring at room temperature, andthen defoamed by stirring under vacuum for 10min.2.2 Fabrication of textured Ti3SiC2 sintered bodyGreen bodies were prepared by slip casting of the slurryin a rotating magnetic field. First, a porous alumina moldwas covered with a membrane filter with a pore diameter of0.2 µm; the slurry was then poured into the acrylic pipes(diameter: 25mm, height: 30mm) placed on the mold. Arelease film composed of polyethylene terephthalate wasattached to the inner walls of each pipe. Next, the mold wasrotated at 20 rpm in a superconducting magnet (JMTD-12T1-NC5, JASTEC), and a strong magnetic field of 12T wasapplied perpendicular to both the casting direction androtating axis. This aligned the c-axis parallel to the castingdirection. After that, cold isostatic pressing was performed at350MPa for 10min.Sintered bodies were obtained using a spark plasmasintering (SPS) machine (SPS-510L, Fuji Electronic Indus-trial Co.). In general, SPS is a sintering method using uniaxialpressing force and the Joule heat via DC pulse current.However, to preserve the pores, pressureless sintering [21,22] was performed using a punch with a diameter larger thanthe inner diameter of the die, as shown in Fig. 1. Thesintering process proceeded as follows: first, under vacuum,the body was heated at 600°C for 10min to burn out the PEI.After restoring the vacuum, the atmosphere was replacedwith argon. It was then heated at a rate of 50°C/min andheld at 1400°C for 1 h. For comparison, the textured densebody was sintered at 1300°C for 10min under a uniaxialcompressive pressure of 40MPa.2.3 Evaluation of textured pressureless-sintered bodyThe porosities of the sintered bodies were calculated usingthe Archimedes method with kerosene as the solvent. Phasecomposition and grain orientation were evaluated by X-raydiffraction (XRD, Smart Lab, Rigaku) using Cu(Kα1)radiation. The samples were cut on planes parallel andperpendicular to the casting direction and polished withemery paper. These surfaces are referred to as the “side” and“top” surfaces, respectively.The side surface was mirror-polished with emery paper,diamond film, and diamond slurry, and then backscatteredelectron (BSE) images were obtained with field-emissionscanning electron microscope (FE-SEM, JSM-7001FA, JSM-7200F, JEOL Ltd.). Moreover, the side surface wasadditionally polished with colloidal silica (particle size:0.04 µm) and analyzed by electron backscattered diffraction(EBSD) with FE-SEM (JSM-6500F, JEOL Ltd./OIM DataCollection, TSL Solutions, Inc.).2.4 High temperature compression test and micro-structure evaluationThe samples were cut from a textured dense body and fromtwo pressureless-sintered bodies with different porosities.Their dimensions were 1.5mm © 1.5mm © 2.25mm, andthe c-axis of the crystal was oriented 45° relative to thecompression axis. Hereafter, they are referred to as “Dense”,“Low-porosity”, and “High-porosity” samples. The top andbottom surfaces of each sample were polished with emerypaper, and the side surfaces were mirror-polished.Compression tests were performed with an Instron 8562universal testing machine. Boron nitride was sprayed onthe sample and on the ground surface of the machine. Themachine was heated to the testing temperature of 1200°C ata rate of 15°C/min, and tests were then conducted at a strainrate of 3 © 10¹4 s¹1, under 4 © 10¹4 Pa. Two of each samplewere compressed to consider the influence of porosity andmicrostructure on deformation behavior, with final strainsof approximately 10% (intermediate deformation) and 20%(large deformation).EBSD analysis and BSE imaging were conducted beforeand after compression. The side surface of each sample wasanalyzed before compression. After compression, a planecut parallel to the compression axis was mirror-polished andevaluated. The obtained BSE images were binarized usingImageJ (NIH) software, and the porosity was calculated.Binarization was employed because the small sample size ledto large errors in the Archimedes method. In these sample,porosity calculated using the Archimedes method was 1.7times higher than the value obtained via binarization.Sintered bodyDiePunchFig. 1 Schematic image of the pressureless sintering.Effect of Porosity on High Temperature Compressive Behavior of Textured Ti3SiC2 Bodies Prepared by Pressureless Sintering 10073. Results and Discussions3.1 Microstructure evaluation of the textured pressure-less-sintered bodyA textured pressureless-sintered body with a porosity of6.5%, measured by the Archimedes method, was evaluated.Figure 2 shows the XRD patterns of the raw powder, sidesurface, and top surface. The bold italicized indices indicatethat the peaks were derived from the (000l ) planes ofTi3SiC2, whereas TiC is indicated by open symbols. On theside surface, strong peaks corresponding to the (hkil ) planes(2ª = 33.9°, 60.2°) were observed, while peaks arising fromthe (000l ) planes (2ª = 30.2°, 40.7°) were observed on thetop surface. This suggests that the c-axes of the body werehighly aligned in the slip casting direction.To quantitatively analyze the texturing, the Lotgeringfactor ( fL) was calculated using eqs. (1) and (2):fL ¼ P � P01� P0ð1ÞP ¼XIð000lÞXIðhkilÞð2Þwhere P is the ratio of the sum of the diffraction intensitiesderived from the (000l ) and (hkil ) planes, and P0 is the Pvalue for a reference sample (the raw powder). The fL valueranges from 0 to 1, where 1 represents perfect texturing. ThefL of the textured pressureless-sintered body was 0.95,indicating strong orientation. This is agreed with the factthat a textured dense sample with sufficient texturing has anfL value of 0.90.The results of the crystal orientation analysis and BSEimages are shown in Fig. 3. Figure 3(a) shows an inversepole figure (IPF) map based on the color key in Fig. 3(b).Figure 3(a) shows the plate-like grains, which are 2–7µm onthe short side and 10–25 µm on the long side. Moreover, the0001 pole figure (PF) in Fig. 3(c) shows that the c-axis of thecrystal is concentrated along the y-axis, which is the castingdirection.Kinked grains are observed in the IPF maps (red arrowsin Fig. 3(a)). The sintering temperature (1400°C) is higherthan 1100–1200°C, the brittle-ductile transition temperatureof Ti3SiC2 [30, 31]. Therefore, it is assumed that the kinkedgrains formed due to the reaction force of the die againstthe thermal expansion of the sintered body. The black areascorrespond to regions of poor crystallinity (white arrows inFig. 3(a)), which are usually grain boundaries, differentphases, and/or strain. However, these pores appeared to havebeen introduced by the sintering process, as the black areaswere round and evenly distributed in the observed area. A0 20 40 60 80Relative intensity, I/I 0Diffraction angle, 2θ ( )(a) Ti3SiC2 powder(b) Pressureless sintered body, Side(c) Pressureless sintered body, TopSlip castdirection00020004000600010000121011101400081015101911201011200014TiCTopSideFig. 2 X-ray diffraction patterns of (a) Ti3SiC2 powder and the sintered body taken from (b) side surface and (c) top surface.(b)10 μm(d) Porosity, P = 6.5%(c)YXSlip cast direction30 μm(a)Slip castdirectionSideYXSideFig. 3 (a) Inverse pole figure (IPF) map of the sintered body and (b) its color-coded map. The red and white arrows in (a) show kinkedgrains and pores, respectively. (c) 0001 pole figure (PF) of (a). (d) BSE image of the textured microstructure. (a) and (d) are taken fromside surface. (online color)E. Sei et al.1008uniform distribution of pores was also observed in the BSEimage (Fig. 3(d)), confirming that the initially intended poreresidue was achieved.3.2 High temperature compression testFigure 4 shows the nominal stress-strain curves of theDense, Low-porosity, and High-porosity samples. Thisdeformation behavior is consistent with the results ofprevious study [13]. The 0.2% proof stresses were221.8MPa, 202.4MPa, and 81.9MPa for the Dense, Low-porosity, and High-porosity samples. Figure 5 shows therelationship between the 0.2% proof stress and porositybefore compression. The stress decreased linearly withincreasing in porosity. Equations (3) and (4) describe theporosity dependence of the mechanical strength in ceramicsand cermets [32–35]:· ¼ ·0Dm ð3Þ· ¼ ·0 expð�kPÞ ð4Þwhere · is the strength of a porous material, ·0 is the strengthof a non-porous material, D (= 1 ¹ P) is a relative density,P is a porosity, and m and k are constant of 3 or greater.The strength of the materials decreases exponentially withincreasing porosity, and this effect becomes more pronouncedonce the porosity exceeds 20%. The results in Fig. 5 arereasonable because the porosity range of these samples(approximately 0.4–13.5%) can be regarded as sufficientlylinear.Figure 6 shows the average work-hardening coefficients(n) for two of each compression test. These values werecalculated in the strain range that could be approximated byeq. (5) from the yielding point:n ¼ dðln · tÞdðln ¾tÞð5Þwhere ·t is the true stress and ¾t is the true strain. Thesecoefficients are generally used to evaluate machinability(e.g., bulging and drawing). However, n-values were usedas indices to quantitatively compare the work hardening,regarded as the stress (d(ln ·t)) required to obtain a certainstrain (d(ln ¾t)). The value for the High-porosity sample was0.55, whereas the Dense and Low-porosity samples exhibitedn-values of 0.34 and 0.32, respectively.This difference is attributed to changes in porosity duringdeformation. The porosity obtained by binarization beforeand after compression are listed in Table 1. The porositiesof the Dense and Low-porosity samples decreased slightly,whereas a substantial decrease was observed in the High-porosity samples. These results indicate that densificationby plastic deformation increases the deformation stress. Thecompression behavior of porous metals can be divided intoelastic, plateau, and densification regions, but the distinctionbecomes less clear with decreasing porosity, as thedeformation stress increases immediately after yielding[36–38].01002003004005000 10 20 30Nominal stress, σn/MPaNominal strain, εn (%)Temperature : 1200℃, Strain rate : 3 10-4 s-1DenseLow-porosityHigh-porosityFig. 4 Compressive stress-strain curves of samples tested at 1200°C.0501001502002503000 5 10 150.2% proof stress, σ0.2/MPaPorosity, P (%)DenseLow-porosityHigh-porosityFig. 5 Relationship between the 0.2% proof stress and porosity before thecompression measured by binarization. The open symbols are the valuesof intermediate samples.00.10.20.30.40.50.6Work hardening coefficient, nDense sampleLow-porosity sampleHigh-porositysampleFig. 6 Average values of work hardening coefficient of samples.Table 1 Porosity of samples before and after the compression measured bybinarization.Effect of Porosity on High Temperature Compressive Behavior of Textured Ti3SiC2 Bodies Prepared by Pressureless Sintering 10093.3 Microstructure evaluation before and after com-pressionFigures 7 and 8 show the IPF maps and 0001 PFs beforeand after compression, respectively. Note that the IPF mapsin Fig. 8 are magnified images compared with those inFig. 7. Kinked grains were frequently observed after largedeformation, which agrees with previous work [6]. Themaximum intensity for each sample decreased throughcompression because kink deformation induced crystallo-graphic misorientation within single grains. However,considering that the compression axis was at 45° from thec-axis, dislocation slips are likely, whereas kink deformationis unlikely. This is assumed to be due to the presence ofnumerous pores and impurities in the polycrystal samples.Figure 9 shows an example of the kink deformationband analysis used to understand the compression behavior.First, the kinked grains were extracted from the IPF maps(Fig. 9(a)), and rotation angle profiles (Fig. 9(b)) weregenerated by measuring the crystal misorientation betweeneach pixel and the starting pixel. Second, approximately 200kink boundaries were measured under the followingconditions: (1) the rotation axis was perpendicular to thec-axis, and (2) the angle change was sharp.Table 2 summarizes the variation in the average numberof kink boundaries and average angle of the kinkboundaries. The average number of kink boundaries wascalculated by dividing the total number of kink boundariesby the number of extracted grains (i.e., number of kinkboundaries per grain). The average number of kinkboundaries increased for the Dense and Low-porositysamples, meanwhile the average angle of the kinkboundaries decreased for all samples. This trend is attributedto the formation of kink boundaries with small angles.Figure 10 shows histograms of kink boundary angles forthe Dense samples before and after compression. Regardlessof the final strain, the distribution shifted toward the smallerangles, and the fraction of kink boundaries below 10°increased. Such formation of kink deformation bandsproduces dislocation-dislocation and dislocation-kink boun-dary interactions, influencing the compressive behavior.X30 μm(e)YXY(f)30 μm(a) YX(b)YXYX(d)30 μm(c)YXCompression directionYXFig. 7 (a), (c), (e) IPF maps and (b), (d), (f ) 0001 PFs. These figures are obtained in (a), (b) Dense, (c), (d) Low-porosity sample, and (e),(f ) High-porosity sample before the compression. The red arrows in IPF maps indicate kinked grains. (online color)E. Sei et al.1010(f) YX(b) YX5 μm(a)YX(d) YX(c)YX5 μm(e)YX5 μmCompression directionYXFig. 8 (a), (c), (e) IPF maps and (b), (d), (f ) 0001 PFs obtained in (a), (b) Dense, (c), (d) Low-porosity sample, and (e), (f ) High-porositysample after the compression up to 20% strain. Note that only IPF maps are magnified images compared to Fig. 7. The red arrows in IPFmaps indicate kinked grains. (online color)noitceridnoisserpmoC30 μm(a) Kink boundary conditionsRotation axis ⊥ c-axisSharp angle changeRotation angle, θ ( )5 μm0 10862 4(b)Distance, L / μm024681012Fig. 9 Method of kink band analysis. (a) IPF map of sample. (b) Extracted IPF map of kinked grain surrounded by the white rectangularin (a) and rotation angle profile of the kinked grain. (online color)Effect of Porosity on High Temperature Compressive Behavior of Textured Ti3SiC2 Bodies Prepared by Pressureless Sintering 1011In the High-porosity samples, the average number of kinkboundaries initially increased and then decreased with furthercompression. This unique trend was not observed in theDense or Low-porosity samples. Figure 11 shows a BSEimage of the intermediately deformed High-porosity sample.Delamination and kink boundaries are indicated by the whiteand black arrows, respectively. This microstructure was onlyobserved in the intermediately deformed sample. Theseresults suggest that the formation and disappearance of tinykink deformation bands may occur during high temperaturecompression of High-porosity samples, which exhibit highn-values. This mechanism may include the migration ofpreexisting kink boundaries, as well as the formation of TiClayers due to the diffusion of Ti and C and the evaporation ofSi. The migration of such kink boundaries could inducedelamination between the Ti ang Si layers, increasing thefree energy of the samples due to new interfaces. Tocomplement this increase, TiC layers could form viadiffusion. The formation of these TiC layers would reducethe number of slip planes (Ti-Si interfaces), potentiallyinhibiting dislocation motion and contributing to higherstrength. Although this phenomenon was observed only inthe High-porosity samples, understanding it is crucial forclarifying kink deformation and kink-band strengthening.4. ConclusionTo investigate the relationship between the compressionbehavior, porosity, and microstructure of Ti3SiC2, wefabricated Ti3SiC2 textured pressureless-sintered bodies andevaluated their microstructures. Furthermore, High tem-perature compression tests were performed on texturedsamples with different porosities, and obtained the followingconclusions:(1) By combining slip casting in a rotating magnetic fieldand pressureless sintering, textured Ti3SiC2 pressure-less-sintered bodies with uniformly dispersed poreswere successfully fabricated.(2) The 0.2% proof stress of Ti3SiC2 decreases linearlywith increasing porosity before compression. However,the work-hardening coefficient of the High-porositysamples was larger than that of the other samples. Thiscan be attributed to densification during compression.(3) Analysis of the kink deformation bands showed thatthe number of kink boundaries per grain increased andthen decreased only in the High-porosity sample duringcompression, suggesting that this phenomenon may beimportant for clarifying kink-band strengthening.AcknowledgmentsThis work was financially supported by JSPS KAKENHI(Grant Numbers JP21H00087, JP21H00110, andJP18H05482) and NIMS Joint Research Hub Program. Apart of this work was also supported by “Advanced ResearchInfrastructure for Materials and Nanotechnology in JapanTable 2 Difference in average number and average angle of kinkboundaries (KBs) by the compression.00.10.20.30.40.5Fraction Kink boundary angle, θkink ( )0-55-1010-1515-2020-2525-3030-3535-4040-4545-5050-5555-6060-6565-7070- 7575-8080-8585-90Before comp.After comp.(a)00.10.20.30.40.5FractionKink boundary angle, θkink ( )Before comp.After comp.(b)0-55-1010-1515-2020-2525-3030-3535- 4040-4545-5050-5555- 6060-6565-7070- 7575- 8080-8585-90Fig. 10 Histograms of the kink boundary angles obtained from densesample before (solid) and after (open) the compression. (a) intermediatesample, (b) large deformed sample.1 μmFig. 11 BSE image of the intermediate compressive specimen of high-porosity sample tested. The black and white arrows show kink boundariesand delamination, respectively.E. Sei et al.1012(ARIM)” of the Ministry of Education, Culture, Sports,Science and Technology (MEXT). Proposal NumbersJPMXP1222HK0034 and JPMXP1223HK0061 (HokkaidoUniversity). A part of this work was conducted at HBXL, ajoint-use facility of Hokkaido University.REFERENCES[1] M.W. Barsoum: The MN+1AXN Phases: A New Class of Solids, Prog.Solid State Chem. 28 (2000) 201–281.[2] M. Radovic and M.W. Barsoum: MAX phases: Bridging the gapbetween metals and ceramics, Am. Ceram. Soc. Bull. 92 (2013) 20–27.[3] J. Gonzalez-Julian: Processing of MAX phases: From synthesis toapplications, J. Am. Ceram. Soc. 104 (2020) 659–690.[4] Y. Shirakami, K. Ikeda, S. Miura, K. Morita, T.S. Suzuki and Y. Sakka:Orientation Dependence of Plastic Deformation Behavior and FractureEnergy Absorption Mechanism around Vickers Indentation ofTextured Ti3SiC2 Sintered Body, J. Jpn. Soc. Powder Metallurgy 67(2020) 607–614.[5] Y. Shirakami, K. Ikeda, S. Miura, K. Morita, T.S. Suzuki and Y. 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