Room Temperature Ultimate Tensile Strength Research Articles

Enhancing the mechanical properties and osteogenic differentiation of Mg-1 wt.%Ho alloy by tailoring microstructures through extrusion temperatures

This investigation was conducted to explore the impact of extrusion temperature on the microstructure, mechanical properties, and osteogenic differentiation of the as-extruded Mg-1Ho alloy. The Mg-1Ho alloy was extruded at three different temperatures, i.e., 320, 350, and 380 °C, leading to variation in its grain size and texture intensity. With decreasing extrusion temperature, a significant increase was achieved in its room-temperature ultimate tensile strength (UTS) and yield strength (YS). After being subjected to an extrusion temperature of 320 °C, furthermore, Mg-1Ho alloy can effectively promote osteogenic proliferation and differentiation, anti-inflammatory, along with osteogenic gene expression. Our findings emphasized that adding extract from Mg-1Ho alloy extruded at 320 °C enhanced the ability of osteogenesis, demonstrating its potential as a biomaterial to improve cell performance and fate.

Effect of Al–5Ti–1B–La intermediate alloy on microstructure and mechanical properties of A356.2 aluminum alloy

This study delves into the effects of Al–5Ti–1B–1La intermediate alloy, a newly developed refinement agent, on the microstructure and mechanical properties of A356.2 aluminum-silicon alloy modified by Al–10Sr. The decomposition of Ti2Al20La, where La element was concentrated in the Al–5Ti–1B–1La intermediate alloy, hardly affected the conventional nucleation mechanism of TiAl3–TiB2; nonetheless, the La element significantly refined the dendritic arms of α-Al. Notably, the secondary dendrite arm spacing was reduced from 49 μm to 27 μm, when 0.025 wt% ∼0.2 wt% Al–5Ti–1B–1La intermediate alloy and 0.014 wt% Al–10Sr modifier was incorporated to the A356.2 aluminum alloy. Although the room-temperature ultimate tensile strength was increased only by 30 MPa, the elongation was remarkably improved from 10% to 26%. The hardness of the alloy was also enhanced from 75 HBW to 84 HBW. The experimental outcomes underscore the efficacy of minimal La element incorporation in enhancing the performance of Al–5Ti–1B intermediate alloy, and the findings are significant for improving the serviceability of automobile wheels made from A356.2 aluminum alloy. The method used in this study can also be employed to regulate the microstructure and enhance mechanical properties of other sub-eutectic aluminum-silicon alloys.

Multi-stage strain-hardening and nano-twinning strengthening Co40Cr22Ni15Fe14Mo4Si3Mn2 multi-principal element alloy

CoCrNiFe multi-principal element alloy (MPEA) plates were prepared by melting and rolling. Thermomechanical treatment (cold rolling and aging) was developed to modify the formation of lattice defects and precipitates. The results show that the Co40Cr22Ni15Fe14Mo4Si3Mn2 MPEA have excellent room temperature ultimate tensile strength and hardness of 1946 MPa and 684 HV0.1. Electron backscatter diffraction (EBSD) and transmission electron microscope (TEM) techniques were used to reveal the microstructure and provide insight into the mechanism. The strengthening mechanism comes from the multiple factors, and most notably, the interaction between nano-twins and Lomer-Cottrell locks. The presence of nano-twins and stacking faults has a significant impact on the strain hardening behavior of the alloy. At the same time, the occurrence and development of deformation substructure dominated by dislocation configuration is the reasons for the material to achieve multi-stage strain hardening (MSSH). This method of realizing MSSH behavior by adjusting microstructure is of great significance in the design and application of FCC MPEA and can be extended to other FCC alloys.

Metal matrix composite with superior ductility at 800 °C: 3D printed In718+ZrB2 by laser powder bed fusion

We investigated the microstructure and mechanical properties of ZrB2 fortified Inconel 718 (In718+ZrB2) superalloy metal matrix composite (MMC), which was produced via Laser Powder Bed Fusion (LPBF). 2 vol% ZrB2 nano powders (below 100 nm in diameter) were decorated on the surfaces of Inconel 718 alloy powders by high-speed blender. Microstructural analysis of the as-printed specimens showed that the ZrB2 decomposed during LPBF, which promoted the formation of homogeneously distributed (Zr, Ni)-based intermetallic and (Nb, Mo, Cr)-based boride nanoparticles in the matrix. The 3D printed In718+ZrB2 has remarkably lower porosity and smaller grain size compared to 3D printed In718 fabricated under the same LPBF conditions. The mechanical performance of the as-printed and heat-treated In718+ZrB2 showed significantly higher room temperature (RT) hardness, RT yield strength (σYS), and RT ultimate tensile strength (σUTS) compared to In718. High-temperature tensile tests at 800 °C showed that In718+ZrB2 has ∼10 times higher tensile ductility with higher σYS (by 10 %) and σUTS (by 8 %) than pure In718.

Effect of high preheating on the microstructure and mechanical properties of high gamma prime Ni-based superalloy manufactured by laser powder bed fusion

Laser powder bed fusion (L-PBF) is an additive manufacturing method with potential applications in the aerospace industry. Currently, IN738LC has been a challenging engineering material to work with as it is inherently brittle due to its high γ′ volume fraction. In this study, crack-free IN738LC was manufactured on a customized L-PBF system capable of preheating to 700 °C. A wide processing parameter range (58–83 J/mm3) could be selected to achieve solid bulk fabrication with a density of 99.95%. The microstructure and mechanical behavior difference between preheating at 200 °C and 700 °C were assessed. In addition to achieving cracking suppression, the high preheating temperature resulted in a strong textured columnar microstructure with finely dispersed carbide particles along the grain boundaries of as-built parts, and superior room temperature ultimate tensile strength of 1612 MPa associated with good ductility of 18% was achieved. Work hardening rate evolution that differed from 200 °C preheating was thought to cause abnormal anisotropic tensile behavior. The influence of preheating on the melt pool morphology, the development of fluid dynamics, and the thermal behavior were discussed according to simulations with the discrete element model (DEM) and volume of fluid (VOF) method.

Laser powder bed fusion of C18150 copper alloy with excellent comprehensive properties

Laser powder bed fusion (LPBF) of copper alloys is expected to revolutionize aerospace propulsion and related industries. This study reports an LPBF-fabricated C18150 copper alloy with excellent comprehensive properties, e.g., thermal conductivity and tensile properties, at both room and elevated temperatures (300 °C, 500 °C). The results show that the nearly full dense specimens are obtained by using optimal process parameters. The microstructure of both the as-built (AB) specimens and the direct aging (DA) specimens at different aging temperatures (480 °C, 530 °C, and 580 °C) with a constant aging time of 4 h mainly consisted of columnar grains, and the grain size remains almost unchanged after aging treatment. The Cr precipitates grow and aggregate with the increase in the aging temperature. The highest room temperature ultimate tensile strength (UTS) of 501 MPa is obtained for specimens aged at 480 °C due to the strong precipitation strengthening effect induced by the tiny and dispersed Cr nano-precipitates. The specimens aging at 580 °C show the highest thermal conductivity of 313 W m−1 K−1 due to the recovery of lattice distortion induced by the Cr atoms dissolution. The trends in tensile properties and thermal conductivity of samples tested at 300 °C are consistent with those at room temperature. When the test temperature is 500 °C, the AB specimens achieve the highest UTS of 274 MPa and thermal conductivity of 259 W m−1 K−1 due to the in-situ precipitation of Cr atoms. This work introduces LPBF C18150 specimens with excellent comprehensive properties and promotes the application of LPBF copper alloys in the industry at different service temperatures.

Grain refinement and modification of an Al–Si–Mg–Ti–Be cast alloy: microstructure and tensile property

In this study, the combined use of grain refinement and modification was studied on a hypoeutectic Al–Si–Mg–Ti–Be cast alloy. The primary α-Al grains were transformed from columnar dendrites in the as-received alloy into fine equiaxed dendrites. Meanwhile, the eutectic Si with irregular morphologies were modified to fine fibrous. The room-temperature ultimate tensile strength is increased by ∼14% from 145 MPa to 165 MPa, while the elongation to fracture is increased from 3% to 5%. The comprehensive enhancement of mechanical properties is due to the synergistic effect of microstructural refinement and isotropic improvement by α-Al grain refinement and eutectic Si modification.

Effect of post process shear straining on structure and mechanical properties of 316 L stainless steel manufactured via powder bed fusion

Powder Bed Fusion (PBF) has become popular despite the fact that PBF-prepared components feature characteristic defects. Their performance, however, can be shifted to the next level by the application of post-processing, advantageously via intensive plastic deformation. The study characterizes the effects of rotary swaging performed at hot, cold, and cryogenic conditions on the (sub)structure and mechanical properties of workpieces of AISI 316 L stainless steel, favourably used in constructions as well as medicine, manufactured by PBF. The workpieces built in the horizontal and vertical directions were analysed to assess their structures, residual strain and stress, density, and porosity; porosity was observed primarily in the horizontally built workpiece also featuring lower density and larger average grain size. Subsequently, the workpieces were subjected to rotary swaging, which contributed to (almost) complete elimination of porosity, evident substructure development, and significant grain refinement – the vertically built workpiece exhibited the avg. grain size of 2.3 µm, 1.8 µm, and 0.1 µm after hot, cold, and cryo swaging. The cryo-swaged sample also exhibited specific texture, room temperature ultimate tensile strength (UTS) of more than 2 000 MPa, and two times higher microhardness compared to the as-build workpiece. All the swaged pieces exhibited significantly improved mechanical properties, even at the testing temperature of 900 °C. • rotary swaging reduced/eliminated printing defects of as-printed workpieces. • structure significantly refined, down to ultra-fine-grain level after cryo-swaging. • specific texture contributed to exceptional mechanical behaviour (at elevated temperatures). • combining powder bed fusion plus rotary swaging is a promising prospective production technology.

Laser-based powder bed fusion of pre-alloyed oxide dispersion strengthened steel containing yttrium

In this study, the pre-alloyed powder Fe-22Cr-5.1Al-0.5Ti-0.26Y (wt%) was prepared by nitrogen atomization and characterized with the aid of focused ion beam (FIB) and transmission electron microscopy (TEM). The oxide dispersion strengthened (ODS) bulk material was successfully fabricated using laser-based powder bed fusion (PBF-LB). Micro-scale Y-Al-O complex oxides and nanoscale Y 2 O 3 @TiN core-shell structures were found in the as-built material. The importance of the presence of residual oxygen in the atomization system and the building chamber for the formation of dual-scale secondary phases was revealed. In addition, the formation mechanism of the dual-scale secondary phases was elucidated by investigating the phase and composition of the as-built ODS steel. Columnar crystals with {001}< 100 > cubic alignments grew epitaxially from the bottom of the molten pool during the PBF-LB process, forming a weak cubic texture in the as-built material. This cubic texture led to anisotropic tensile properties of the as-built material, where the room-temperature ultimate tensile strength in the XY-45° direction was higher than that in the building direction (Z). Our work provides a feasible scheme to shorten the preparation process of ODS alloys, which is usually carried out using complicated means. • The Y-containing pre-alloyed powder was prepared by nitrogen atomization. • Primary precipitates in the powder were characterized by FIB and TEM. • Residual oxygen participated in the alloying reaction in the molten metal. • Formation mechanisms of oxides and cubic texture were revealed.

Laser powder bed fusion of high-strength maraging steel with concurrently enhanced strength and ductility after heat treatments

Laser powder bed fusion (LPBF) has been demonstrated as a metal additive manufacturing technique that can manufacture high-performance metal components with complex shapes directly from raw powder materials. Although 18Ni-300 maraging steel has been extensively employed in this process, a significant trade-off has always existed between strength and ductility when using traditional solution and ageing heat treatments. This study addresses this problem by introducing a heat treatment combination that includes hot isostatic pressing (HIP) before the conventional ageing treatment. The experimental results demonstrated an enhancement of the relative density from 99.6% in the as-built conditions to 99.96% after HIP, although a small number of residual gas pores remained. The subsequent ageing treatment after HIP had a negligible effect on the reopening of these closed defects. Microstructure observations revealed that a fully martensitic structure can be obtained after HIP, and austenite reversion was less sensitive with the HIP + ageing treatment (HAT) compared to direct ageing treatment (DAT). Grain growth and alloying homogenisation also occurred during HIP. Massive nanoscale precipitations were formed both after DAT and HAT; quantitative analysis based on TEM observation indicated that the size of these precipitates was larger after subjecting to HAT. The room-temperature ultimate tensile strength and elongation to failure after HAT were approximately 6% and 100% higher than DAT, confirming the simultaneous enhancement of the strength and ductility after HAT. The findings of the present study offer insights into heat treatment approaches that can overcome the strength-ductility trade-off of LPBF-manufactured 18Ni-300 maraging steel, while also providing an alternative strategy for obtaining the simultaneous improvement of strength and ductility through heat treatments.

Fabricating Ti–22Al–25Nb intermetallic with ductility higher than 25% by advanced printing technique: Point-forging and laser-deposition

PF-LD is an advanced printing technique which introduces point-forging (PF) into the process of conventional laser-deposition (LD). Ti–22Al–25Nb intermetallic fabricated by PF-LD technique presented the excellent combination of room-temperature ultimate tensile strength (UTS: 1050.1–1169.3 MPa) and elongation after failure (EL: 20.8%–25.7%). An elaborately designed controlled trial by simultaneous use of LD and PF-LD techniques was employed to investigate the effect of PF on LD microstructural evolution. The results pointed out that the occurrence of static recrystallization (SRX) was the essential reason for the ultra-high mechanical properties. Both mechanisms of continuous-SRX (CSRX) and discontinuous-SRX (DSRX) played an important role in grain refinement. By in-situ forging and subsequent re-heating, the coarse columnar grains were first broken into fine equiaxed grains through progressive subgrain rotation. After two-pass PF-LD, the solidification texture <100>//DD disappeared while no obvious recrystallization texture was found. In subsequent PF-LD process, micron-scale CSRX grains were developed within original equiaxed grains through repeated polygonization and progressive subgrain rotation while DSRX grains appeared along grain boundaries driven by the differential dislocation density. We elucidated the excellent mechanical properties by detailed microstructural analysis. The results revealed that the finer equiaxed grains and the reasonable phase composition (O + BCC) greatly retarded the process of crack nucleation and propagation resulting in the typical micro-void accumulation ductile fracture while both high-density dislocations and finer recrystallized grains were beneficial to strength enhancement.

The Effect of the Pre-Existing VC on the Evolution of Precipitate and Mechanical Properties in the H13 Steel.

To further improve the mechanical properties of H13 steel at room and high temperatures, its precipitates were regulated based on the Thermo-Calc results. Scanning electron microscope (SEM), electron backscattering diffraction (EBSD), transmission electron microscope (TEM), and X-ray diffraction (XRD) Rietveld refinement were used to study the effect of the intercritical annealing on the microstructure and mechanical properties of H13 steel. The results show that the intercritical annealing at 850~95 °C increased the VC volume fraction from 2.23 to 3.03~3.48%. Increasing the VC volume fraction could inhibit the M7C3 precipitation from 10.01 to 6.63~5.72% during tempering. A large amount of VC also promoted the M23C6 precipitation during tempering at higher dislocation densities. The intercortical annealing simultaneously increased the elongation of H13 steel. An excellent combination (room temperature: ultimate tensile strength (UTS) of 898 MPa and total elongation (TEL) of 19.35%, 650 °C: UTS of 439 MPa, and TEL of 27.80%) could be obtained when intercritical annealing is performed at 900 °C. Meanwhile, after aging at 650 °C for 128 h, the room temperature UTS and TEL decreased by only 31 MPa and 0.52%, respectively.

Enhancing strength via nano-lattice defects in La0.008Al0.08FeCoCrNiMn high-entropy alloy produced by rapid solidification, cold rolling and annealing

Multiple lattice defects play a crucial role in improving the mechanical properties of FeCoCrNiMn high entropy alloys (HEAs). In the present work, the strength and hardness of the La0.008Al0.08FeCoCrNiMn HEA were first increased and then decreased during the annealing process due to the competitive mechanism between the recrystallization softening and precipitated phase hardening. Especially, a superior room temperature ultimate tensile strength (1403 MPa) and a fracture strain (9.1%) have been obtained, which was treated by quenching in the liquid metal, cold rolling at room temperature, and annealing at 600 °C for 32 min. The characterizations and analysis indicate that the fundamental cause of the strengthening is attributed to the synergistic effects of nano-sized precipitated particles (mean size: 20.2 nm), dislocation cells, and nano-twins (∼10 nm in thickness) together with Lomer-Cottrell locks. Meanwhile, the effects of different lattice defects on strength contribution have been quantified.

Influence of cooling rates on microstructure and tensile properties of a heat treated Ti2AlNb-based alloy

In the present study, a two-phase Ti 2 AlNb-based alloy with a nominal composition of Ti–22Al–25Nb (at%) comprising the dominant O + B2/β phase was explored. The microstructural evolution and tensile properties are studied by applying different heat treatment methods of water-cooling (WC, 140 °C/s) and furnace-cooling (FC, 0.08 °C/s) after heat treatment at 1015 °C for 40 min, followed by aging treatment at 800 °C for 1, 5, and 100 h. The results indicated that the morphologies of solution-treated alloys after different cooling methods have a significant distinction. The WC alloy consists of a continuous B2/β phase and a few remnant O phase, whereas the FC alloy comprises a mass of lath O phase and discontinuous B2/β phase. The Widmanstätten O + B2 structures were generated in the following aging treatment. The α 2 phase was not detected during the heat treatments in the present work. The B2 phase and O phase in the aged WC and FC alloys follow the classical orientation relationship: ( 110 ) B 2 / / ( 001 ) O , [ 1 ‾ 11 ] B 2 / / [ 1 1 ‾ 0 ] O . The room-temperature ultimate tensile strength (UTS) and elongation to failure (EL) of the FC and aged FC alloys are higher than the WC and aged WC alloys, except for the 100 h-aging condition. On the contrary, the high-temperature UTS and EL of the aged WC alloys are higher than the aged FC alloys. The existence of the O/O phase boundaries, the coarsening of the B2 grain boundary and discontinuous precipitation harmed the performances of the studied alloys. Beyond that, the fracture mode of the explored alloys with different heat treatment methods was also analyzed. • The morphologies of solution-treated Ti 2 AlNb-based alloys after different cooling methods have a significant distinction. • The B2 phase and O phase in the studied alloys follow the classical orientation relationship: 110B2//001O, [111]B2//[110]O. • Tensile properties and fracture mode are significantly influenced by different cooling rates and aging treatments. • The O/O boundaries, coarsening of the grain boundary and discontinuous precipitation harmed the properties of the alloys.

Microstructure and mechanical properties of an ODS ferritic steel with very low Cr content

An ultra-low Cr oxide dispersion strengthened (ODS) steel with the composition of Fe-5Cr-4.5Al-0.6Zr (hereinafter abbreviated as 5CrAlZr ODS steel) were proposed and manufactured via mechanical alloying (MA) and hot isostatic pressing (HIP), followed by hot forging treatment. TEM results indicate that a large amount of fine δ-Y4Zr3O12 particles were formed within the grains and along the grain boundary, additionally, Y6ZrO11 and Al2Y4O9 nano-particles with larger size were also detected. The mean particles diameter (dp), the mean inter-particle spacing (λ) and number density (nv) of the nano-oxide particles in the 5CrAlZr ODS steel are about 10 nm, 80 nm and 1.23 × 1022 /m3, respectively. The room temperature ultimate tensile strength (UTS) and the total elongation (TE) of the fabricated 5CrAlZr ODS steel are 875 MPa and 21%, respectively, which are higher than those of traditional 5Cr-2W-0.24V steels. The UTS and TE of 5CrAlZr ODS steel at 700°C are 234 MPa and 58%, respectively. The strengthening mechanisms underlying were also discussed.

Mechanical properties of rolled and aged AA6061 sheets at room-temperature and cryogenic environments

We prepared AA6061 sheets by room-temperature rolling and low-temperature aging. We tested the tensile mechanical properties of the sheets at room temperature and cryogenic (173 K) temperature. The maximum difference between the cryogenic ultimate tensile strength and room-temperature ultimate tensile strength was 50 MPa for the sheets subjected to a rolling reduction ratio of 50% and aging at 393 K for 10 h. As the rolling reduction ratio increased, the lattice friction stress, dislocation strengthening, and precipitation strengthening of the material gradually approached a limiting value, thus reducing the difference between the strengths of the samples tensile tested at room temperature and cryogenic temperature.

Microstructure evolution and formation mechanism of a crack-free nickel-based superalloy fabricated by laser engineered net shaping

In this study, the crack-free parts have been successfully fabricated by Laser Engineered Net Shaping (LENS) based on a Ni-Co-Cr-Al-Ti-Fe-Nb-Mo nickel-based superalloy powder, and its microstructure evolution and formation mechanism were investigated. The results revealed that the microstructure along the deposition direction is stray dendrites with disordered growth direction in the bottom two layers, epitaxially growing elongated columnar dendrites dominating the whole cross-section of the as-deposited, fine equiaxed grains in the upper of the last layer, respectively. Moreover, it can be found that although the as-deposited layer contains many high angle grain boundaries, no cracks can be observed. According to the chemical composition and phase analyses, it can be concluded that crack-free microstructure is ascribed to the homogeneous distribution of elements and the formation of single-phase γ in the as-deposited. The effect of 1.34 Al, 1.37 Ti, 0.41 Nb, and 0.50 Mo (wt%) on the formation of low melting point substances is discussed. The room-temperature ultimate tensile strength is about 807 MPa, while the high-temperature ultimate tensile strength is 654 MPa.

Microstructures and tensile properties of Ti2AlNb and Mo-modified Ti2AlNb alloys fabricated by hot isostatic pressing

The Ti2AlNb and Mo-modified Ti2AlNb alloys were fabricated by hot isostatic pressing, and then underwent annealing treatment at 800 °C for 1, 2 and 3 h respectively. To evaluate the tensile properties of the two kinds of alloys, tensile tests were conducted at ambient temperature and 650 °C in this study. For the Ti2AlNb alloy, the room-temperature ultimate tensile strength (UTS) was 700–900 MPa, and the highest elongation to failure (εf) reached 6.2% after aging for 2 h at 800 °C. Since the Mo addition promoted the precipitation of the coarse B2+O colony structure near the grain boundary, the Mo-modified Ti2AlNb alloy exhibited decreased UTS and εf at room temperature. As for the high-temperature performance of both the Ti2AlNb and Mo-modified Ti2AlNb alloys, the UTS reached approximately 700 MPa and the εf exceeded 3.0%. Meanwhile, the two kinds of alloys presented the same tendency that both the high-temperature UTS and εf increased firstly and then decreased as the aging time increased. Among them the specimens after aging at 800 °C for 2 h for both alloys acquired the highest UTS and εf. Moreover, the Mo-modified alloy exhibited a better high-temperature ductility than that at room temperature, which is associated with the B2↔O phase transformation during the loading at 650 °C. The Mo addition effectively refined the lath of the precipitates in the grain and the grain size of the matrix, and it induced abundant dislocations. Thus, the Mo-modified Ti2AlNb alloy aged for 1 and 3 h exhibited superior high-temperature mechanical properties than those of the Ti2AlNb alloy.

The Elevated-Temperature Strength Enhancement of a Low-Cost β Titanium Alloy Through Thermomechanically-Induced Phase Transformation

The effects of temperature and thermomechanical loading on the tensile strength and hardness were studied for a rolled, low-cost metastable β titanium alloy, Ti-13Cr-1Fe-3Al (wt.%). Tensile tests were performed at temperatures between room temperature (RT) and 410°C. The results indicated that the ultimate tensile strength (UTS) decreased with increasing temperatures up to 300°C. However, the UTS was 1400 MPa at 410°C, which was approximately 150% higher than the RT UTS. It is believed that the formation of nanoscale ω and α precipitates, identified using transmission electron microscopy, hindered the dislocation motion, which resulted in the exceptionally high UTS at 410°C. However, ductility was maintained, as the elongation-to-failure (ef) was ~ 10% at 410°C. Dynamic mechanical analysis suggested that phase transformations occurred between 370°C–475°C. To evaluate the effect of the phase transformations on the hardness, the as-received material was heat treated at 400°C, 450°C, and 500°C for 2 h, which resulted in hardness values of approximately 340 Hv, 380 Hv, and 470 Hv, respectively. However, the greatest hardness value (500 Hv) was exhibited by the as-received material after it was tensile tested at 410°C. This suggested that both temperature and loading history affected the phase transformations. As all the samples exhibited a ductile fracture mode, this work indicates that it is possible to maintain both high strength and adequate ef for Ti-13Cr-1Fe-3Al (wt.%).

Microstructure, tensile properties and creep behavior of high-Al TiAlNb alloy using electromagnetic cold crucible continuous casting

Newly designed Ti–47Al–10Nb alloy was prepared at growth rates ranging from 0.3 mm/min to 1 mm/min under power of 45 kW using electromagnetic cold crucible continuous casting technique. The macro/microstructure, tensile properties and creep behavior are studied. Results show that this alloy can be directionally solidified at growth rates from 0.3 mm/min to 0.7 mm/min, and this alloy exhibits the β-solidification at growth rates from 0.3 mm/min to 1 mm/min. The lamellar spacing decreases with the increasing of growth rate, and the relationship between lamellar spacing and growth rate can be fitted by d=371.2V−0.56. The directional solidification structure has little effect on room temperature ultimate tensile strength, and the creep properties strongly depend on the directional solidification structure. At the optimum preparation parameters of 0.5 mm/min and 45 kW, this alloy exhibits the good room-temperature tensile properties with ultimate tensile strength 562 MPa and elongation 1.42%, and the minimum strain rate is 4.31 × 10−8s−1 during creep at 800 °C/200 MPa. Moreover, in directional solidification structure, the plastic incompatibility of lamellar colonies leads to the local stress concentration at the steps of vertical colony boundary, which promotes the formation of cavities and cracks at colony boundary.