Volume Fraction Of Laves Phase Research Articles

Effect of post weld heat treatment on weld metal microstructure and hardness of HFCA-TIG welded ASTM-B670 high temperature alloy joints

In this investigation, the effect of post weld heat treatment (PWHT) conditions on weld metal (WM) microstructure and hardness of ASTM B670 alloy joints are studied for gas turbine engine applications. This high temperature alloy was joined using high frequency compressed arc TIG (HFCA-TIG) welding process. The precipitation hardening was performed on ASTM-B670 alloy joints directly after welding (DPH); after solutionizing the welds at 980 °C (980ST+PH) and at 1065 °C (1065ST+PH). The WM of ASTM-B670 alloy showed better response to PWHT in minimizing the Laves phases and enhancing the WM hardness of joints. The DPH, 980ST+PH and 1065ST+PH joints showed 55.63%, 58.80% and 64.08% enhancement in hardness of WM compared to as welded (AW) joints owing to the precipitation of hardening phases after PWHT. The 1065ST+PH joints revealed higher hardness of WM than DPH and 980ST+PH joints It is attributed to the complete dissolution of Laves phases in WM causing more Nb available for precipitation hardening of WM. Nevertheless, the PM hardness of 1065ST+PH joints are lower than 980ST+PH joints owing to the severe grain growth. The HFCA-TIG welds showed volume fraction of Laves phase up to 5.10% in WM which is 80.38% and 36.25% lower than constant current TIG (CC-TIG) and pulsed current TIG (PC-TIG) welds. It is attributed to magnetic compression and high frequency pulsation of arc which minimizes input of heat in welding and offers greater refinement of WM.

Microstructure evolution and strengthening mechanisms in Ni36Co30Cr11Fe11Al12-Nb high entropy alloys

To reveal the microstructure evolution and the strengthening mechanism, the Ni36Co30Cr11Fe11Al12-xNbx (x = 2, 4, 6, 8, 10 at%) high entropy alloys (HEAs) were designed. Phase composition, phase prediction, tensile properties and strengthening mechanisms were researched in detail. Results show that the alloys consist of face-center cubic (FCC) phases and Laves phases. The regularity of several factors, such as electronegativity difference and d-orbital energy level, predicted that the volume fraction of Laves phase is increased with the increase of Nb/Al ratio. The yield strength and the strain of Ni36Co30Cr11Fe11Al8Nb4 HEAs are 670 MPa and 16.5%, respectively. The alloy shows the typical hypoeutectic structure. The effects of solid solution strengthening and the interfacial strengthening were analyzed. When the Nb content> 6 at%, the effect of the interfacial strengthening is stronger compared with solid solution strengthening The FCC-Laves interface shows the higher barrier strength. The micrographs of dislocation structures show that the extensive dislocation pileups appear at the incoherent interface. The incoherent interface may shear easily and attract gliding dislocations due to its low shear strength, which explains the sharply decrease of the ductility.

Modified heat treatment and related microstructure-mechanical property evolution of arc melting additively manufactured GH4169 Ni-based superalloy

GH4169 Ni-based superalloy was prepared by wire arc additive manufacturing (WAAM) in this study. Similar to the microstructure of other additive manufactured superalloys, the additively manufactured GH4169 alloy suffered from a high-volume fraction of Laves phase, which is detrimental to the alloy’s mechanical properties. To solve this problem, two different post heat-treatment approaches were selected to improve the tensile properties at both room and elevated temperatures, which are the one with solution treatment temperature at 950 °C and the modified one with solution treatment at 1150 °C, respectively. Detailed phase analysis during different heat treatment processes was conducted using both scanning and transmission electron microscopes. Comparative tensile tests were also conducted at both room temperature and 650 °C to analyze the role of the different microstructures on the deformation responses of the prepared samples. By increasing the solution treatment temperature from 950° to 1150°C, the volume fraction of Nb-rich Laves phase dramatically decreased, and the previously Laves-phase-trapped Nb contributed to the formation of the strengthening γ″ phase. As a result, the tensile strength of this modified treated alloy is significantly improved at both room and elevated temperatures. Additionally, due to lower volume fraction of the Laves phase, the elongation of the modified treated alloy at room temperature is improved by ∼35%. These findings provided new insights into the post-heat treatment approaches of the WAAM Ni-based superalloy.

Development of a high strength, low density and corrosion resistant novel FeCrMoNb1.5Ti0.5 complex concentrated alloy

The present work deals with the microstructure, mechanical properties and corrosion behavior of a FeCrMoNb1.5Ti0.5 complex concentrated alloy (CCA). The aforementioned alloy was fabricated by vacuum arc melting technique. The observed density and lattice parameters of the as-cast alloy are 7.821 g/cm3 and 3.179 ± 0.003 Å, respectively, which follow the rule of mixture. The phase evolution, chemical composition, and microstructure in the as-cast condition, as well as after annealing treatment at 800°C, 1000°C, and 1200°C, were investigated through XRD, TEM, and SEM-EDS. The XRD and TEM analyses confirmed the presence of BCC structure with minor amount of TiCr2 type and NbCr2 type C14 Laves phases. Instrumented micro-indentation and corrosion testing were performed in the as-cast and annealed specimens. The microhardness of the as-cast alloy was 825 HV and it increased to 1102 HV after annealing at 1200ºC for 20 h. This peak hardness was achieved after annealing at 1200ºC due to the presence of a large volume fraction of Laves phase. Potentiodynamic polarization tests of the as-cast and as-annealed specimens revealed outstanding corrosion resistance of the CCA compared to stainless steel. This is attributed to better microstructural homogeneity and reduced elemental segregation after annealing.

Phase formation and mechanical features in (AlCoCrFeNi)100-xHfx high-entropy alloys: The role of Hf

Tailoring the alloy composition, which thus adjusts the phase selection and the generation of intermetallic phases to obtain the desired mechanical properties, is a suitable approach in structural applications. To modify the mechanical properties of equimolar AlCoCrFeNi high entropy alloy (HEA), we design a few (AlCoCrFeNi)100-xHfx HEAs (x = 0, 2, 4 and 6, at.%) and evaluate the effect of Hf additions on the phase evolution and mechanical properties. The additions of Hf transform the microstructures of HEA series from a single-phase BCC solid solution to a hypoeutectic microstructure, in which the hypoeutectic microstructure is composed of primary BCC phase and the eutectic structure with alternately growing BCC and Laves phases. Meanwhile, several criteria (δ-Δχ and Δχ) are employed to predict the formation possibility of intermetallics in the present HEA system. When raising Hf additions, the volume fraction of Laves phase increases from 0 to 33.8 vol.%, thus resulting in an increment in compressive yield strength from about 1273 MPa to ∼2023 MPa with degrading the plasticities of HEA series to some extent. This resultes from solid solution strengthening, second phase strengthening and fine grain strengthening. This work will open up other doors for HEA design with superior properties.

Novel as-cast NiAlCoFeNb dual-phase high-entropy alloys with high hardness

• A novel class of NiAlCoFeNb HEAs were synthesized by vacuum arc melting. • These HEAs consist of NiAl-rich B2 phase and FeNb-rich hexagonal Laves phase. • The hardness increases with the incremental volume fraction of Laves phase. • The equiatomic Ni 20 Al 20 Co 20 Fe 20 Nb 20 HEA has ultrahigh hardness of ∼ 818 HV. The microstructure, phase constitution and microhardness of Ni 20 Al 20 Co 20 Fe 20 Nb 20 , Ni 25 Al 25 Co 20 Fe 20 Nb 10 and Ni 30 Al 30 Co 20 Fe 15 Nb 5 high-entropy alloys (HEAs) synthesized by vacuum arc melting have been investigated. These as-cast HEAs have a dual-phase structure including intermetallic NiAl-rich B2 phase and FeNb-rich hexagonal Laves phase, and the Nb increase leads to more fraction of Laves phase. Ultrahigh hardness of ∼ 818 HV was achieved in the equiatomic Ni 20 Al 20 Co 20 Fe 20 Nb 20 dual-phase HEA, which is consisted of 61.8 vol% Laves phase and 38.2 vol% B2 phase.

Effects of Ta and Ti content on microstructure and properties of multicomponent Co–Ni-based superalloys

The content and the existing form of refractory elements significantly affect the performance in service of superalloys, which has gained extensive attention in this field. In this study, basic influence rule of diverse Ta and Ti contents on the microstructure and properties of the novel γ′ phase strengthened Co–Ni-based superalloys is clarified by thermodynamic calculation and experimental research. Under the premise of a total Ta and Ti content of 5 at%, increasing Ta content elevates the solvus temperature of γ′ phase and volume fraction of Laves phase, and also reduces the volume fraction of β phase in the as-cast alloys. Moreover, the average size of γ′ phase goes down and the coarsening of γ′ phase is inhibited simultaneously in the alloy after aging treatment. Consequently, increasing the content of Ta can enhance the microstructure stability and elevates the Vickers hardness and yield strength of the alloy. However, the density and cost of the alloy have to be raised. Meanwhile, the variation of Ta and Ti contents affects the oxidation performance of the alloys by influence the volatilization of W and Mo oxides. 2Ta3Ti and 3Ta2Ti alloys possess favorable oxidation resistance at 1050 °C. Considering the effect of Ta and Ti elements and normal performance requirements of Ni-based superalloys, 3Ta2Ti alloy has more impressive engineering application prospects. This work provides a solid foundation for optimizing the composition and improving the properties of Co–Ni-based superalloys.

Effects of circular oscillating laser on microstructure and mechanical property of nickel-based superalloy by laser melting deposition

GH3536 nickel-based superalloy was fabricated by circular oscillating laser melting deposition and traditional Gaussian laser melting deposition in the present investigation. The effects of circular oscillating laser beam on the macro morphology, microstructure evolution and mechanical properties of the GH3536 alloy were studied. The results show that the dilution ratio and heat affected zone of circular oscillating laser are smaller than those of Gaussian laser. The oscillating laser beam drives the melt flow, destroys the growth of columnar dendrites, promotes the diffusion of elements and inhibits the precipitation of Laves phase. The volume fraction of Laves phase is about 30.03% lower than that of Gaussian laser. Increasing the oscillating frequency or amplitude can refine the grain. The ultimate tensile strength of GH3536 alloy deposited by circular oscillating laser in parallel and vertical directions is 683.64 ± 17.02 MPa and 687.23 ± 5.89 MPa respectively, which is 6.57% and 9.96% lower than that of Gaussian laser, respectively; The elongation in parallel and vertical directions is 35.86% and 38.1%, which is 91.36% and 41.22% higher than that of Gaussian laser, respectively. The circular oscillating laser can significantly improve the toughness of GH3536 alloy and improve the difference of mechanical properties in different sampling directions.

The formation and dissolution mechanisms of Laves phase in Inconel 718 fabricated by selective laser melting compared to directed energy deposition and cast

In this study, we explain why the amount of Laves phase in Inconel 718(IN718) manufactured by selective laser melting (SLM) unexpectedly increases under extremely rapid solidification and clarify its distinct dissolution behavior during heat treatment based on a comparative analysis of laser directed energy deposition (L-DED)-built and cast IN718. Compared with the cast and L-DED, SLM has much higher cooling rate, which greatly improves the dendrite growth rate and the solute trapping during the solidification process of molten pool. Thus, more Nb atoms are trapped in the matrix, and less Nb atoms are expelled to form inter-dendritic Laves phase in SLM-built IN718. However, the volume fraction of Laves phase is the highest in SLM-built IN718, which is attributed to the lower Nb concentration in the Laves phase and few Nb-rich region. During homogenization treatment, the dissolution of Laves phase is controlled by three-dimensional diffusion process at the early stage, and then is mainly controlled by the interface reaction process. After homogenization, there are still many tiny carbides, oxides, and nitrides undissolved both along the grain boundaries and inside the grains.

Multimaterial Additive Manufacturing of Graded Laves Phase Reinforced NiAlTa Structures by Means of Laser Metal Deposition

Recently, the additive manufacturing (AM) technology laser metal deposition (LMD) has gained a lot of attention for processing crack prone high temperature materials such as nickel‐based superalloys or intermetallics. A feasibility study on LMD of a graded transition from binary ß‐NiAl to Ni50Al42Ta8 is presented with the aim to show the possibility of manufacturing ß‐NiAl‐based structures with a spatially resolved microstructure and subsequently tailored mechanical properties. For achieving this, the alloys Ni50Al50 and Ni50Al42Ta8 are coinjected into the process zone and the powder feeding rates are adapted in a layerwise manner. Due to preheating temperatures of up to 1000 °C, the transition can be manufactured with high relative density and a low degree of cold cracking. Scanning electron microscopy of the transition zone shows the formation of a fine dendritic microstructure consisting of ß‐NiAl dendritic and NiAlTa interdendritic regions. Large area energy‐dispersive X‐ray analysis reveals a gradient in NiAlTa Laves phase content with increasing build height. The observed volume fraction of Laves phase corresponds well to reported values from cast ingots. Finally, hardness measurements along the build‐up direction show an increase in hardness from 300 HV0.1 to 680 HV0.1 indicating a tremendous increase in tensile strength.

Effect of solution temperature on the microstructure and mechanical properties of Hastelloy X superalloy fabricated by laser directed energy deposition

In this study, the effect of solution temperature on the microstructure and mechanical properties of Hastelloy X fabricated by laser directed energy deposition (LDED) was investigated. As a result, the microstructure of as-deposited (AD) sample was mainly coarse columnar grains directionally growing along the deposition direction. Due to the segregation of Mo and Cr, a lot of Laves phase precipitates in the inter-dendritic. With the increase of solution temperature, the volume fraction of Laves phase gradually decreases. When the solution temperature increased to 1200 °C, the grains of the LDED Hastelloy X superalloy exhibited fully recrystallization, and then became coarse with the solution temperature of 1225 °C. With the dissolution of the Laves phase, the microhardness of the samples drops from 231 ± 5 HV to 211 ± 5 HV. The room temperature tensile results reveal that the as-deposited sample with irregular and long-striped Laves phase presents the worst tensile strength (652 ± 10 MPa) and elongation (30 ± 2%). After heat treatment, the strength and elongation of the LDED Hastelloy X superalloy gradually increased with increasing the solution temperature. When the solution temperature was 1200 °C, the tensile strength of the sample reached the maximum value of 720 ± 1 MPa. With the increase of solution temperature, the elongation increased and then reached the maximum value of 47 ± 2% with heat-treated at 1225 °C. The tensile fracture of LDED Hastelloy X superalloy with solution treatment presented a ductile fracture pattern.

Integrated control of molten pool morphology and solidification texture by adjusting pulse duration in laser additive manufacturing of Inconel 718

Both single-track and bulk Inconel 718 samples were fabricated using pulsed laser additive manufacturing to investigate the effect of pulse duration on the molten pool morphology and the solidification texture. For single-track depositions, clad width, remelting depth, dilution ratio and peak molten pool temperature decrease, while clad height, clad area, minimum temperature and molten pool lifetime increase with the increase of the pulse duration. The fusion line of the molten pool in transverse direction is pan-like at a short pulse duration (20 ms), and gradually turns circular (60 ms) as the pulse duration increases. For bulk samples, uniform grains with a strong fiber texture are established for a short pulse duration. In contrast, alternatively distributed coarse grains in the overlapping region and fine grains at the center of the molten pool with a weak cube texture are obtained for a long pulse duration. In addition, samples fabricated with short pulse durations contain less volume fraction of Laves phase than that with long pulse durations. Pulsed laser additive manufacturing has the potential for texture control and in-situ production of components with functional graded textures.

Evolution of microstructure and mechanical properties of 9Cr ferrite/martensite steels with different Si content after long-term aging at 550 °C

In view of developing novel alloys for applications in advanced Generation IV lead-cooled fast reactor (LFR) fuel cladding materials, four 9Cr ferrite/martensite (F/M) heat resistant steels with different Si content were developed. In the present work, the long-term thermal aging of 9Cr F/M steels was carried out in air at 550 °C for 500, 1000, 2000 and 5000 h. The microstructural evolution was investigated based on OM, SEM, EBSD and TEM technologies. The changes of mechanical properties after thermal aging were evaluated by room temperature tensile test. During long-term aging, the microstructures of all four steels exhibited highly thermal stability, and M23C6 carbides and MX carbonitrides also remained unchanged. Meanwhile, after aging for 5000 h, a new Fe2W-type Laves phase formed in all four steels with an average size of 94.8 ± 17 nm in 9Cr-1Si steel. The tensile properties of all samples aged for 2000 h exhibited almost no change compared with the as-received ones. However, after thermal exposure for 5000 h, the strength of all four 9Cr F/M steels increased due to the precipitation strengthening effect of the small Laves phase particles. Silicon exerted a certain degree of solid solution strengthening effect for 9Cr F/M steels. The volume fraction of Laves phase increased with the increase of Si content. As the Si content was 1%, residual high-temperature ferrite was found in the microstructure, but it has no detrimental effect on the mechanical properties of 9Cr F/M steels studied in the present work. Comprehensively considering the microstructure and mechanical properties, the suitable addition of Si content did not exceed 0.7%.

Coarsening of Laves phase and creep behaviour of a Re-containing 10% Cr-3% Co-3% W steel

The coarsening of Laves phase in a Re-containing 10% Cr-3% Co-3% W steel during both creep and ageing at 923 K was investigated. The depletion of W solutes from the ferrite matrix is accompanied with the precipitation of Laves phase, wherein creep strain accelerates both these processes. The equilibrium W content in the ferritic matrix of 1.24 wt% and the volume fraction of Laves phase of 1.6% is reached after 500 h of creep and 1000 h of ageing. This is related to lower activation energy for W diffusion upon creep testing. The coarsening of Laves phase obeys Ostwald ripening and can be described in terms of Lifshitz-Slyozov-Wagner theory: d 4 – d 0 4 = K p (t-t 0 ), where K p = 3.70–3.80 × 10 −11 μm 4 s −1 for both creep and ageing suggesting that the coarsening of these particles should be controlled by grain boundary diffusion. No strain-induced coarsening of Laves phase is observed. Growth of the Laves phase particles located on the lath boundaries and the high-angle boundaries of the blocks, packets and prior austenite grains occurs in independent manner. The Laves phase particles located on the high-angle boundaries are susceptible to coarsening that leads to appearance of the particles with dimensions >200 nm. The Laves phase particles located on the lath boundaries dissolve with a low rate. Dense chains of Laves phase on the lath boundaries retain up to high creep time giving a significant contribution to creep behaviour.

Effect of niobium addition upon microstructure and tensile properties of CrMnFeCoNix high entropy alloys

Abstract Nb-doped CrMnFeCoNix (x = 0.2, 0.4, 0.6, 0.8 and 1) high entropy alloys were prepared by vacuum induction melting. The effects of Ni and Nb content on the microstructure evolution and tensile properties of the alloys were investigated. With increasing Ni content, the CrMnFeCoNix alloy changed its structure from a combination of face-centered cubic phase and σ phase to a single face-centered cubic phase. The yield strength, ultimate tensile strength and ductility of CrMnFeCoNix alloys first increased and then decreased with the increase of Ni content. Compared with other CrMnFeCoNix alloys, CrMnFeCoNi0.8 HEA has shown superior mechanical properties, exhibiting a high yield strength (240.9 MPa), ultimate tensile strength (527.5 MPa) and an impressive elongation-to-failure (62.5%). The addition of Nb significantly increased the volume fraction of Laves phase in the CrMnFeCoNi0.8 alloy, which further enhanced the tensile properties of CrMnFeCoNi0.8 high entropy alloys. The yield strength and ultimate tensile strength of the CrMnFeCoNi0.8Nb0.2 alloy were determined to be 406.9 MPa and 662.8 MPa, representing a 68.9% and 25.6% increase over CrMnFeCoNi0.8 alloy.

Influence of arc constriction current frequency on tensile properties and microstructural evolution of tungsten inert gas welded thin sheets of aerospace alloy

The main objective of this investigation is to study the influence of arc constriction current frequency (ACCF) on tensile properties and microstructural evolution of aerospace Alloy 718 sheets (2 mm in thickness) joined by constricted arc TIG (CA-TIG) welding process. One variable at a time approach of design of experiments (DOE) was used, in which ACCF was varied from 4 to 20 kHz at an interval of 5 levels while other parameters were kept constant. The joints welded using ACCF of 4 kHz exhibited superior tensile properties extending joint efficiency up to 99.20%. It is attributed to the grain refinement in fusion zone leading to the evolution of finer, discrete Laves phase in interdendritic areas. An increase of ACCF above 12 kHz caused severe grain growth and evolution of coarser Laves phase in fusion zone. Alloy 718 welds showed more obvious tendency for Nb segregation and Laves phase formation at higher levels of ACCF due to the slower cooling rate. The volume fraction of Laves phase was increased by 62.31% at ACCF of 20 kHz compared to that at 4 kHz, thereby reducing the tensile properties of joints. This is mainly due to the stacking of heat input in weld thermal cycles at increased levels of ACCF.

Laves phase control of inconel 718 superalloy fabricated by laser direct energy deposition via δ aging and solution treatment

In order to achieve the microstructure homogeneity at a lower temperature and improve the mechanical properties, a novel post heat treatment was introduced to Inconel 718 fabricated by laser direct energy deposition (LDED), by means of δ aging treatment + solution treatment. The microstructure analysis shows that the fully precipitation of δ phase in LDED Inconel 718 superalloy can “cut” the long strip Laves phase into small pieces. According with the δ phase solution treated at 1020 °C for 30 min, only tiny particle Laves phase was remained. The equilibrium volume fraction of Laves phase after δ phase solution treatment is about 1%, which is much lower than that of the as-deposited sample or the sample only solution treated at 1020 °C. Due to the solution strengthening and precipitation of γ″ phase during aging treatment, the tensile strength of δ aging + δ solution + double aging treated samples was 10.27% higher than that of directed solution + double aging treated samples, as well as a 31.38% and 52.71% increases in elongation and the reduction of area during tensile tests.

Effect of Heat Input on Evolution of Microstructure and Tensile Properties of Gas Tungsten Constricted Arc (GTCA) Welded Inconel 718 Alloy Sheets

The significant effect of heat input on the microstructural characteristics and tensile properties of 2-mm-thick Inconel 718 alloy sheets joined by gas tungsten constricted arc welding process was investigated systematically. It involves the application of magnetic arc constriction technique to solve the heat input-related metallurgical problems in gas tungsten arc welding of Inconel 718 alloy such as segregation of Nb and laves phase evolution in weld metal region which drastically reduces the weld mechanical properties. Heat input range was used from 495 to 585 J/mm by varying Main Current from 60 to 80 A at distinct levels of 5 A. The average secondary dendrite arm spacing was increased from 6.31 to 8.92 μm, revealing the corresponding cooling rate between 2087 and 720 °C/s. Superior tensile properties were obtained at an optimum heat input of 518 J/mm. It exhibited 98.16 and 78% of base metal strength and ductility. It is attributed to the grain refinement in fusion zone microstructure and the evolution of lower amount of laves phase with finer and discrete morphology. The average size and volume fraction of laves phase for the current sample were 3.12 μm and 7.68%. The benefits of magnetic arc constriction and Delta Current pulsing were not achieved at higher heat input.

Influence of Vanadium on the Microstructure of IN718 Alloy by Laser Cladding.

A deleterious Laves phase forms in the solidified structure of Inconel 718 (IN718) alloy during laser cladding. However, effective removal methods have not yet been identified. In this study, we first added the IN718 alloy cladding layers with a trace amount of vanadium (V, 0.066 wt.%). Then, we studied the solidification structure of cladding layers using a confocal laser scanning microscope and scanning electron microscopy. The microstructure and Laves phase morphology were investigated. The distribution of niobium (Nb) was observed by experiment as well. We found that V is evenly distributed in dendrites and interdendritic zones. A more refined dendrite structure, reduced second dendrite arm spacing and lower volume fraction of Laves phase were observed in the solidification structure. The results of linear energy-dispersive X-ray spectroscopy (EDS) indicate that the concentration of Nb decreases with an increasing of the distance from the Laves phase. The V-containing sample displayed a relatively slower decreasing tendency. The IN718 alloy sample was harder with the addition of V. In addition, the porosity of the sample decreased compared with the blank sample. The presented findings outline a new method to inhibit the Nb segregation in IN718 alloy during laser cladding, providing reference significance for improving the performance of IN718 alloy samples during actual processing.

Deformation and strength characteristics of Laves phases in titanium alloys

The superior reinforcement nature of Laves phases make them suitable for high-strength applications. Therefore, investigations on the deformation and strength characteristics of Laves phases are useful in development of an improved Laves phase-reinforced alloy. In this work, the Vickers micro-indentation method is used to evaluate and compare the deformation and strength characteristics of a hexagonal close-packed Laves phase (C14-type) in Ti-35Zr-5Fe-6Mn (wt%) and a face-centered cubic Laves phase (C15-type) in Ti-33Zr-7Fe-4Cr (wt%), considering the same volume fraction of Laves phase (~7.0%) in these alloys. Moreover, the effects of higher volume fraction of Laves phase (19.4%) on indentation-based deformation features are evaluated in Ti-35Zr-5Fe-8Mn (wt%). Remarkably, dislocation activity and plastic deformation features are evident in the C15-type Laves phase, whereas the C14-type Laves phase strongly blocks dislocation motion. Therefore, the C15-type Laves phase improves plastic deformability, whereas the C14-type Laves phase improves strength characteristics of Laves phase-reinforced alloys.