Cluster Formula Research Articles

Design of Ultra-Strong As-Cast Titanium Alloy at 600 ℃ by Using Cluster Formula

Design of Ultra-Strong As-Cast Titanium Alloy at 600 ℃ by Using Cluster Formula

Soft solution state and hard aging state of Inconel 718 reached via optimized precipitation elements using cluster formula approach

The superior high-temperature performance of Inconel 718 is originated mainly from the precipitation strengthening via Nb, Al, and Ti alloying. Inappropriate contents of the precipitation elements may lead to over-strengthened solution state and insufficiently strengthened aging state. We have previously identified the alloy composition formula [(Nb,Al,Ti)1-(Ni,Fe,Cr,Mo)12](Ni,Fe,Cr,Mo)5 using the cluster formula approach, where the 18-atom structural unit is composed of a nearest-neighbor cluster, centered by one precipitation elements, plus five glue atoms situated at the next neighbors. On the basis of this formula, the present work designs a series of alloys using (Nb,Al,Ti) = 0.93, 1, and 1.06, with 4.9 and 5.5 wt % Nb, 0.68 and 0.5 wt % Al, and 1.10 wt% Ti corresponding to the upper-to-middle ranges in the ASTM standard. In particular, when the total number of atoms in the formula is equal to one, (Nb0.6Al0.2Ti0.2), the alloy is soft at the solution state (σUTS = 825 MPa < 965 MPa of the standard and EL = 70.3 % > 30 %) and reaches high strength levels after aging (σUTS = 1400 MPa > 1240 MPa and EL = 23.4 % > 12 % at room temperature, σUTS = 1100 MPa > 965 MPa and EL = 10.2 % > 5 % at 923 K). This alloy also shows the lowest coarsening rate of 4–7 × 10−3 nm3 s−1 after long-term aging at 923 K, lower than the prevailing coarsening rate of about 16 × 10−3 nm3 s−1.

Design of Ti−7Al−2V alloy with high specific strength by using cluster formula

A near-α Ti−7Al−2V alloy was designed using cluster formula approach and prepared by laser additive manufacturing, whose specific strength is better than that of Ti−6Al−4V alloy. Its composition formula α-{[Al−Ti12](AlTi2)}15+β-{[Al−Ti14](V3)}2 features an enhancedα-Ti by increasing α unit proportion of 15/17 (with respect to 12/17 of Ti−6Al−4V alloy) and stabilized β-Ti via V alloying. This alloy possesses a good laseradditivemanufacturing processibility. At the as-deposited state, the microstructures are composed of fine basket-weave regions, coarse basket-weave regions and ultrafine αWidmanstättenlath regions. The surface roughness of coarse basket-weave regions is much smaller than that of fine basket-weave regions and ultrafine αWidmanstättenlath regions. The α-phase distribution in fine basket-weave regions is more uniform than that in the coarse basket-weave regions. Its ultimate tensile strength of 971−1005 MPa, yield strengthof 891−921 MPa andelongation of 4.5%−6.6% are close to those of Ti−6Al−4V alloy, and particularly, its specific strength of 224−232 kN·m/kg is better than that of Ti−6Al−4V alloy.

A high-temperature Ti-6.8Al-6.8Zr-2.3V-2.1Mo-0.7Nb alloy suitable for laser-additive manufacturing

A high-temperature Ti-6.8Al-6.8Zr-2.3V-2.1Mo-0.7Nb alloy suitable for laser additive manufacturing is designed on the basis of the cluster formula of Ti–6Al–4V, composed of twelve α-[Al–Ti12](AlTi2) units and five β-[Al–Ti12Zr2](AlV1.2Mo0.6Nb0.2) ones, featuring enhanced β stability via Zr, Mo, Nb, and V co-alloying. Using pre-alloyed powders, this alloy shows a fine surface roughness about 83 μm, which is comparable to that of reported Ti–6Al–4V. The as-deposited alloy exhibits a typical bimodal basket-weave microstructure and superior mechanical properties at room temperature (ultimate tensile strength (UTS) of 1348 MPa, yield strength (YS) of 1253 MPa, and elongation of 4.4%) as well as at 600 °C (UTS of 657 MPa, YS of 578 MPa, and elongation of 44.6%), which are comparable to wrought-state high-temperature Ti alloys. At 650 °C, its UTS of 424 MPa and YS of 337 MPa still maintains a high level.

Effects of Si variation and Zr addition on the microstructure, oxidation resistance and mechanical property at 1523 K of Nb-Si-Ti/Zr/Hf-Cr/Al high-entropy superalloys

The present work investigated the influences of the variation of Si content and the minor amount of Zr addition on the microstructure, oxidation resistance and mechanical property at 1523 K of Nb-Si-Ti/Zr/Hf-Cr/Al high-entropy superalloys systematically. Alloy compositions with Nb-21.6(Ti/Zr)-3.1Hf-(9.4–15.6)Si-6.3Cr-3.1Al-1.0B (at. %) were designed using a cluster formula approach to realize the substitution of similar elements, in which these alloys were solid-solutionized at 1573 K for 24 h and then aged at 1273 K for 24 h. It was found that all these aged alloys are mainly composed of BCC-Nb solid solution (Nbss), Nb5Si3 and Cr2Nb phases, where the increase of Si content and the addition of Zr could significantly increase the volume fraction of Nb5Si3 in a form of coarse and primary particles. Consequently, high-Si alloys possess outstanding mechanical property at high temperature, as evidenced by the fact that the yield strength (σYS = 373 MPa) at 1523 K of high-Si/Zr alloy containing 15.6 at. % Si and 1.6 at. % Zr is much higher than that (σYS = 266 MPa) of the low-Si alloy with 9.4 at. % Si and 0 Zr. It is mainly ascribed to the existence of primary Nb5Si3 particles, besides the eutectic microstructure composed of Nbss and Nb5Si3, as well as fine Cr2Nb precipitates in Nbss. Moreover, a minor amount of Zr substitution for the Ti is conducive to the phase transition of α-Nb5Si3 to γ-Nb5Si3. Thus, this high-Si/Zr alloy exhibits an improved oxidation resistance after 50 h-exposure at 1523 K, due to the lowest mass gain of about 80.9 mg/cm2. The constitutions of oxide scales in these alloys were characterized and compared, from which it was found that the better oxidation resistance is closely related to the formation of dense oxide scales. This work will provide a new approach to obtain an optimum combination of mechanical property and oxidation resistance of superalloys through multi-component alloying.

Achieving high strength in dual-phase Ti-6.4Al-4.4Mo-2.1Zr-0.6Si alloy using cluster formula design

In this paper, a near-α dual-phase Ti-6.4Al-4.4Mo-2.1Zr-0.6Si alloy, modified from TC11 alloy, and prepared by copper-mold suction casting, achieves the high strength level, with the ultimate tensile strength of 1323 MPa, yield strength of 1222 MPa, and specific strength of 289 kN m/kg, even superior to the reference TC11 prepared in the same condition and comparable to high-strength β-Ti alloys, at the expense of a low as-cast elongation of 1.2%. Its composition formula α-{[Al-Ti12](AlTi2)}14 + β-{[Al-Ti13Zr1](Mo2Si1)}3 fall within the composition framework previously determined for TC11: the α and β formulas still satisfy the ratio of 14: 3, while the β part, originally [Al-Ti13.2Zr0.8](Mo1.5Si0.5Ti1) for TC11, is further enhanced using Zr, Mo and Si co-alloying. This alloy is characterized by a basket-weave microstructure containing extensive fine α′ martensite needles plus small amounts of α and remnant β phases and very few α'' phases.

Intuitive graphical presentation of cluster-plus-glue-atom model to obtain composition formulas of industrial alloys

The composition of a solid-solution alloy resides in its chemical unit, consisting of a nearest-neighbor cluster and a few next-neighbor glue atoms according to the cluster-plus-glue-atom model. However, the identification of the glue atoms in the chemical unit requires complex calculations. The present work simplifies this process into an intuitive graphical representation for binary face-centered-cubic solid solutions. By presenting graphically the relationship between the number of glue atoms and the solute-over-solvent atomic radius ratio, in combination with the alloy composition, the specific form of the chemical unit for any given alloy can be directly read from the graph. Two types of cluster formulas are distinguished. One is to idealize the chemical unit with the nearest neighbor completely occupied by solvent atoms, such as the [Zn-Cu12] cluster for α Cu-Zn brass that leads to a chemical unit [Zn-Cu12]Zn4. The second one, more general, is to consider the chemical unit with mixed nearest-neighbor occupations in accordance with Cowley’s short-range-order parameter α1, as exemplified by the presence of a [Zn-Cu9.4Zn2.6] cluster in Cu68.9Zn31.1 alloy that gives [Zn-Cu9.4Zn2.6]Zn1.4Cu2.6. The two formulas are actually identical in chemistry, for both units share the same chemical formula Cu12Zn5, which corresponds to the most widely used brass grade C26000 (70Cu-30Zn). This graphical presentation can also be extended to multi-component alloys through the classification of similar elements as exemplified in superalloy Inconel 718, thus providing a universal means for understanding the compositions of industrial alloys.

Composition optimization of inconel 718 via cluster formula and experimental verification

Superalloys feature multi-elements and complex elemental ranges, which makes the proper composition selection difficult. In fact, more strict composition standards generally apply in practical productions. The objective of this paper is to understand and eventually to renew the composition standard via example of the most common grade Inconel 718. We have recently shown that t he alloy chemistry originates from a nearest-neighbor cluster [center-shell] plus a few next-neighbor glue atoms, or expressed in cluster formula [center-shell] (glue atoms). By grouping the elements into Ni¯ = (Ni, Co, Cu, Fe), Cr¯ = (Cr, Mn, Si, Mo), and Nb¯ = (Nb, Al, Ti), it is found that the reported alloys fall within a narrow composition zone Ni¯11.0-13.0-Cr¯3.5-4.5-Nb¯1 confined by cluster formulas of 16 and 18 atoms. This composition zone is also expressed in terms of 288-atom supercluster formulas, Ni¯198-208-Cr¯63-72-Nb¯16-18, which leads to coordinated elemental variations in wt.%: 69.0 ≤ Ni + Co + Cu + Fe ≤ 72.7; 19.8 ≤ Cr + Mn + 1.7 Si + 0.6 Mo ≤ 22.8; 8.7 ≤ Nb + 3.2 Al + 1.9 Ti ≤ 9.8. Within this composition zone, Ni¯206-Cr¯65.5-Nb¯16.5 is further pinpointed and validated by our own experiments to possess the optimal match of strength and plasticity both at room and at 923 K.

Composition interpretation of Co-Cr industrial alloys using cluster formula approach

Composition interpretation of Co-Cr industrial alloys using cluster formula approach

High-strength Ti-Al-V-Zr cast alloys designed using α and β cluster formulas

Ti-Al-V-Zr quaternary titanium alloys were designed following α-{[Al-Ti12](AlTi2)}17−n+β-{[Al-Ti12Zr2](V3)}n, where n=1–7 (the number of β units), on the basis of the dual-cluster formula of popular Ti-6Al-4V alloy. Such an alloying strategy aims at strengthening the alloy via Zr and V co-alloying in the β-Ti unit, based on the original β formula [Al-Ti14](V2Ti) of Ti-6Al-4V alloy. The microstructures of the as-cast alloys by copper-mold suction-casting change from pure α (n=1) to α+α′ martensite (n=7). When n is 6, Ti-5.6Al-6.8V-8.1Zr alloy reaches the highest ultimate tensile strength of 1,293 MPa and yield strength of 1,097 MPa, at the expense of a low elongation of 2%, mainly due to the presence of a large amount of acicular α′ martensite. Its specific strength far exceeds that of Ti-6Al-4V alloy by 35%.

Composition formula of Al-TMs high-entropy alloys derived by cluster-plus-glue-atoms model and its experimental verification

High-entropy alloys (HEAs) are based on solid solutions which characterized by chemical short-range ordering (CSRO), but there is no accurate structural tool to address CSRO characteristic, which obstacles precise composition design for HEAs. In this study, based on the cluster-plus-glue-atoms model, the composition law of Al-TMs (TMs, transition metals) HEAs with BCC and FCC structures was revealed. In BCC structure, with five elements in equi-atomic ratio, the composition formula of Al-TMs HEAs can be expressed by a cluster formula [Al-M14]Al3, and in non equi-atomic ratio can be expressed by [Al-M14]Al, where M is the average atom of the TMs. But in FCC structure, both Al-TMs HEAs with five elements in equi-atomic and non equi-atomic ratios can be expressed by a cluster formula [Al-M12]Al. To confirm the effectiveness of cluster formula for Al-TMs, two alloys were designed, [Al-Ti4V3Nb4Mo3]Mo and [Al-Ti3V3Nb4Mo4]Al. Results show that the [Al-Ti3V3Nb4Mo4]Al alloy has both higher strength and higher plastic deformation at room temperature. Besides, [Al-Ti3V3Nb4Mo4]Al alloy shows slower soften effect at 800 °C, contributed to its higher strength. By substituting Ta for some of Mo, the strength of [Al-Ti3V3Nb4Mo3Ta]Al at room temperature and high temperature drastically decreases, suggesting that Ta element deteriorates the properties of Al-TMs alloys.

High-strength and energetic Al2Ti6Zr2Nb3Ta3 high entropy alloy containing a cuboidal BCC/B2 coherent microstructure

The present work developed a novel high-strength and energetic Al 2 Ti 6 Zr 2 Nb 3 Ta 3 high entropy alloy (HEA) containing a BCC/B2 coherent microstructure. The microstructural evolution of BCC/B2 with both the aging temperature (873 ~ 1073 K) and aging time (up to 200 h) was investigated, from which it was found that the cuboidal BCC nanoparticles are coherently-precipitated into the B2 matrix in 873 K-aged state due to a moderate lattice misfit ( ε ~ - 0.76%). The increase of aging temperature could destroy the BCC/B2 coherency and accelerate the formation of brittle Zr 5 Al 3 phase. Especially, the BCC/B2 microstructure exhibits an excellent thermal stability, as evidenced by the fact that these cuboidal BCC nanoprecipitates were not coarsened obviously at 873 K with the particle size from r ~ 10 nm in 24 h-aged state to r ~ 20 nm in 200 h-aged state. This alloy possesses prominent mechanical properties with high yield strength at both room temperature ( σ YS = 1193 MPa) and elevated temperatures (1060 MPa at 873 K and 106 MPa at 1273 K), where the high strength was discussed in light of the precipitation strengthening mechanism. Importantly, the current alloy has an ultrahigh combustion calorific capacity with a value of 10240 J·g -1 , showing a great potential to be used as novel high-performance energetic structural materials. • A high-strength and energetic HEA was developed with the cluster formula approach. • High-strength of alloy was realized by forming a BCC/B2 coherent microstructure. • The BCC/B2 coherent microstructure exhibits a higher thermal stability at 873 K. • The alloy has an ultrahigh combustion calorific value of 10240 J·g -1 .

Composition optimization of Zr55Cu30Al10Ni5 bulk metallic glass using cluster formula approach

Compositions of typical binary and ternary bulk metallic glasses have previously been interpreted via a cluster formula approach, i.e., a good glass former is formulated by a nearest-neighbor cluster matched with one or three glue atoms, with a free electron number per unit formula approaching 24. In this study, a classical quaternary glass composition Zr55Cu30Al10Ni5, representative of bulk metallic glasses of complex chemistry and dual-glassy structure, is interpreted and optimized using a dual-cluster formula approach, i.e., a chemical formula representing two single-cluster formulas. First, the number of atoms in the dual-cluster formula is estimated from combinations of all possible single-cluster formulas of the major devitrification phase CuZr2, which ranges from 28 to 34. Second, the free electron number of each element is estimated using the Cu-Zr single-cluster formulas. Third, the reference composition Zr55Cu30Al10Ni5 is approximated into integer forms of 27 to 36 atoms and their free electron numbers are calculated using the assigned free electron numbers of the elements. The so-formulated compositions are examined for glass forming abilities via copper-mold arc melting. The atomic densities, the critical temperatures, the HV hardness, the volume fractions of the glassy phase in the ingots, and the activation energies of crystallization all point to a 32-atom chemical formula Zr17Cu10Al3Ni2 (Zr53.13Cu31.25Al9.38Ni6.25) as the optimal glass former, with its electron number per unit formula falling slightly below 48. This work confirms the 24-electron rule for single-cluster formulas and provides an easy route towards understanding the complex chemistries of bulk metallic glasses via multiple single-cluster formulas.

Achieving high-temperature strength and plasticity in near-α Ti-7Al-3Zr-2V alloy using cluster formula design

We here report a Ti-7Al-3Zr-2V alloy, designed following cluster formula approach and prepared by laser additive manufacturing, whose mechanical performance is superior to commonly used Ti-6Al-4V alloy both at as-deposited state and at 600 °C. Its composition formula α-{[Al-Ti12](AlTi2)}15+β-{[Al-Ti12Zr2](V3)}2 features an enhanced α unit proportion of 15/17 (with respect to 12/17 of Ti-6Al-4V) and stabilized β-Ti via Zr and V alloying. This alloy shows a good laser-additive-manufacturing processibility. At the as-deposited state, its ultimate tensile strength of 1060 MPa, yield strength of 976 MPa, and particularly elongation of 14.9% are all better than those of Ti-6Al-4V. At 600 °C, its ultimate tensile strength of 545 MPa, yield strength of 497 MPa, and elongation of 39.7% far exceed the performance of Ti-6Al-4V. After the tensile tests at 600 °C, the α plate size and its volume fraction remain basically unchanged, in sharp contrast to Ti-6Al-4V.

Effect of processing parameters on formability, microstructure, and micro-hardness of a novel laser additive manufactured Ti-6.38Al-3.87V-2.43Mo alloy

A novel Ti-6.38Al-3.87V-2.43Mo alloy was designed with a cluster formula of 12[Al-Ti12] (V0.75Mo0.25Ti2)+4[Al-Ti12](Al3) by replacing Ti with Mo/V on the basis of the Ti-Al congruent alloy. The effects of laser power and scanning speed on the molten pool size, surface roughness, relative density, microstructure, and micro-hardness of single-track and bulk Ti-6.38Al-3.87V-2.43Mo samples prepared via laser additive manufacturing (LAM) were investigated. The results show that processing parameters significantly affect the formability, microstructure, and micro-hardness of the alloy. With decreasing laser power from 1,900 W to 1,000 W, the relative density is decreased from 99.86% to 90.91% due to the increase of lack-of-fusion; however, with increasing scanning speed, the relative density does not change significantly, but exceeds 99%. In particular, Ti-6.38Al-3.87V-2.43Mo samples of single-track and bulk exhibit a good formability under an input laser power of 1,900 W and a scanning speed of 8 mm·s-1, and display the lowest surface roughness (Ra=13.33 µm) and the highest relative density (99.86%). Besides, the microstructure of LAM Ti-6.38Al-3.87V-2.43Mo alloy coarsens with increasing laser power or decreasing scanning speed due to the greater input energy reducing the cooling rate. The coarsening of the microstructure decreases the microhardness of the alloy.

Effect of Nb glue atom in the cluster formula on the microstructure and mechanical properties of Ti-Mo alloy

The effect of Nb in the glue site of the cluster-plus-glue atom model formula on the microstructure and mechanical properties of Ti-Mo alloy was investigated. Phase and microstructural analysis were performed by X-ray diffraction and electron backscatter diffraction. Tensile properties were also examined. A small amount of secondary martensitic α” and ωath nano particles were precipitated in the β matrix of both alloys, due to to the inhomogeneous distribution of Mo and/ or Nb caused by segregation, which formed local regions with high- and low-stability of the β phase. The elastic modulus was significantly reduced to 56.9 ± 3.08 GPa, while the elastic admissible strain was substantially improved. The increased β stability and suppression of the ωath phase led to no significant change in both the yield and ultimate tensile strengths, and the brittle fracture behavior. The alloy can be a potential alternative of the conventional orthopedic implant materials in orthopedic applications.

Compositional interpretation of high elasticity Cu–Ni–Sn alloys using cluster-plus-glue-atom model

The D022 or L12-γ′ phase strengthened Cu–Ni–Sn alloys possesses a characteristic microstructure, exhibiting the distribution of precipitated phase with smaller size on a spinodal decomposition structure, which leads to that the composition of the precipitated phase and Cu matrix cannot be precisely measured and restriction of the accurate compositional design of the alloys. The present work initials to introduce the cluster-plus-glue-atom model for compositional interpretation of the industrial Cu–Ni–Sn alloys, and then optimizing the cluster formula according to the measured composition of the relevant precipitated phases. Moreover, the solid solution content of Ni or the precipitation content of Sn are calculated based on the optimized cluster formula, and establishing the relationship between the alloy composition and properties. It indicates that the strength mainly relays on the precipitation content of Sn while the conductivity depends on the solid solution content of Ni, which is also suitable for the Cu–Ni–Sn–Zn (Co) alloys or Cu–Ni–Al alloys with similar characteristics. Additionally, the ratio of strength/resistivity increases in the alloys as the increasing Sn content under the premise of close to 3 of Ni/Sn (or (Ni + Co)/Sn) atomic ratio, but the discontinuous precipitation is easily to generate. Therefore, the improved properties of the alloys cannot be attained via the reducing ratio of Ni/Sn (or (Ni + Co)/Sn) atomic ratio solely. Based on the above, this work provides theoretical support and application methods for the compositional design and performance prediction of coherent D022 or L12-γ′ phase strengthened alloys.

Enthalpic interaction promotes the stability of high elastic Cu-Ni-Sn alloys

Enthalpic interaction between the elements determines the stability of the local structures in the alloy system. Multicomponent synergistic effect is expected to improve the thermal stability and the relevant properties by regulating the enthalpic interaction. In this work, the composition of Cu-Ni-Sn alloys is explained by introducing the cluster-plus-glue-atom mode, and the strong and weak enthalpic interaction elements Si and Zn, respectively, are chosen for multi-componentization of Cu-Ni-Sn alloys. The results demonstrate that the synergistic effect of Zn and Si improves the stability of both the Cu matrix and D022 or L12-γ′ phase, inhibits the discontinuous precipitation effectively and gains a notable higher strength-over-resistivity ratio (HR / ρR) than the Cu-15Ni-8Sn (wt. %) (C72900) alloy. After adding Si and Zn, the reinforcing enthalpic interaction between the elements is the crucial factor for the stability enhancement of the alloys, and it is embodied by two aspects: (a) the reducing elastic strain energy in the solution treated alloys; (b) the more homogeneous surface potential and the higher work function in the age treated alloys. Additionally, Compared with the Cu80Ni15Sn5 alloy that based on the ideal cluster formula, the Cu79.68Ni15.63Sn4.69 alloy, based on the modified cluster formula: {[Cu-CuxNi12-x]Cu3}a{[Sn-NiyCu12-y]Sn3}16-a, possesses a preferable thermal stability whatever solution treated or age treated state, and exhibits a decreasing amount of discontinuous precipitation although has a slightly lower HR / ρR, which is beneficial to the improvement of the workability of the alloys. The modified cluster formula is more suitable for the compositional design of Cu-Ni-Sn alloys. The work provides an effective theoretical and experimental basis for the composition design of high stability Cu-Ni-Sn alloys.

Design and properties of novel Ti–Zr–Hf–Nb–Ta high-entropy alloys for biomedical applications

The novel high-entropy alloys (HEAs) with compositions of (Ti1/3Zr1/3Hf1/3)15(Nb1/2Ta1/2)x (x = 3, 5) for biomedical applications have been designed and synthesized, using the cluster formula approach. The present HEAs have a single body-centered-cubic (BCC) solid-solution structure and possess prominent mechanical properties of high compressive yield strength (834–890 MPa) and microhardness (287–293 Hv), large plasticity (>45%) under compression, as well as low Young's moduli (56–68 GPa). Also, these HEAs exhibit good bio-corrosion resistance, as revealed by a low corrosion rate at the order of 10−4 mm/year and the low passive current densities of 10−2 – 10−1 A/m2, which are attributed to the formation of passive films consisting of Ti-, Zr-, Hf-, Nb-, and Ta- oxides. The high cell viability and proliferation of bone-forming MC3T3-E1 cells on the HEAs are comparable to those on the Ti–6Al–4V alloy, indicating their good biocompatibility. The present work demonstrates the great potential of these novel Ti–Zr–Hf–Nb–Ta HEAs for biomedical applications.

Microstructure and mechanical properties of laser additive manufactured novel titanium alloy after heat treatment

A novel α+β titanium alloy with multi-alloying addition was designed based on the cluster formula 12[Al-Ti12](AlTi2)+5[Al-Ti14](AlV12Mo06Nb02) which was derived from Ti-6Al-4V. The nominal composition of this novel alloy was determined as Ti-6.83Al-2.28V-2.14Mo-0.69Nb-6.79Zr. In this study, the novel alloy and Ti-6Al-4V alloy samples were prepared by laser additive manufacturing. The microstructure, micro-hardness, room/high temperature tensile properties of the as-deposited samples were investigated. Compared to Ti-6Al-4V, the novel alloy has much higher room and high temperature (600 °C) tensile strengths, which are 1,427.5 MPa and 642.2 MPa, respectively; however, it has a much lower elongation (3.2%) at room temperature because of the finer microstructure. To improve the elongation of the novel alloy, heat treatment was used. After solution at 960 °C or 970 °C for 1 h followed by air cooling and aging at 550 °C for 4 h followed by air cooling, a unique bi-modal microstructure which contains crab-like primary α and residual β phase is obtained, improving the compression elongation by 80.9% compared to the as-deposited samples. The novel alloy can be used as a high-temperature and high-strength candidate for laser additive manufacturing.