Abstract
It is well known that semi-solid forming could only obtain coarse-grained microstructure in a few alloy systems with a low melting point, such as aluminum and magnesium alloys. This work presents that semi-solid forming could also produce novel bimodal microstructure composed of nanostructured matrix and micro-sized (CoFe)Ti2 twins in a titanium alloy, Ti62Nb12.2Fe13.6Co6.4Al5.8. The semi-solid sintering induced by eutectic transformation to form a bimodal microstructure in Ti62Nb12.2Fe13.6Co6.4Al5.8 alloy is a fundamentally different approach from other known methods. The fabricated alloy exhibits high yield strength of 1790 MPa and plastic strain of 15.5%. The novel idea provides a new insight into obtaining nano-grain or bimodal microstructure in alloy systems with high melting point by semi-solid forming and into fabricating high-performance metallic alloys in structural applications.
Similar content being viewed by others
Introduction
Nanostructured materials often exhibit low ductility at room temperature and very limited or lack of work hardening due to limited dislocation capability1. One feasible and practical approach to enhance the ductility of nanostructured materials is to form bimodal microstructure with coexistence of nanoscale and micron-sized grains2. The formation of such a bimodal microstructure could provide nanostructured materials with both high strength and ductility compared to single-phase nanostructured materials or conventional coarse-grained materials3. In general, such bimodal microstructure can be obtained by several routes, such as thermo-mechanical treatment4, powder consolidation5, recrystallization method6 and rapid solidification7. Especially, many titanium alloys with bimodal microstructure have been prepared by rapid solidification and exhibits high strength and large plasticity7,8,9,10,11,12,13. For example, the Ti60Cu14Ni22Sn4Nb10 alloy has strength of 2400 MPa and plastic strain of 14.5%7 and Ti63.375Fe34.125Sn2.5 exhibits strength of 2650 MPa and a plasticity of 12.5%12. The typical metallurgical characteristics for obtaining bimodal-microstructure titanium alloys by rapid solidification are preferential nucleation and growth of micron-sized body-centered cubic (bcc) β-Ti dendrites from high-temperature melts followed by rapid solidification of the remaining liquid with highly dense random-packed structure to obtain nanostructured matrix7,8,9,10,11,12,13.
As one of the important materials processing technologies, the core feature of semi-solid forming includes special non-dendrite solid microstructure and moderate forming temperature locating between solidus and liquidus temperature14. Integrated across multi-disciplines, a series of semi-solid forming methods, coupling with casting, extrusion, forging, rolling and so on, have been developed spontaneously. However, current semi-solid forming usually includes a relatively complicated process for preparing semi-solid alloy slurry and it unfortunately can only produce coarse-grained microstructure in a few alloy systems with a low melting point15, such as aluminum alloys and magnesium alloys. So far, it is impossible to form nanocrystalline or bimodal microstructure in alloy systems having a high melting point, for example titanium alloys.
According to binary alloy phase diagrams16, a typical eutectic transformation occurred at eutectic temperature can be expressed as α + β ↔ L, where α and β are two solid components and L is a liquid state. Currently, the liquid phase in semi-solid forming based on eutectic transformation has a relatively loose random-packed structure in aluminum alloys and magnesium alloys17. This is the reason why current semi-solid forming cannot obtain nanocrystalline or bimodal microstructure. As such, a question arises: if a liquid phase, resulted from preferential eutectic reaction of two solid phases in a multi-phase alloy system with a high melting point, has a highly dense random-packed structure, does the composition of this liquid phase tend to form a nanostructured phase/microstructure in process of solidification17,18? Undoubtedly, the semi-solid state consisting of such a liquid phase is different from those in the aforementioned semi-solid forming. As supported by the extensive studies (e.g. refs 17,18) on the formation of nanostructure or glassy alloys by rapid solidification, a semi-solid state with highly dense random-packed structure is easy to be obtained in multicomponent alloy systems having a high melting point. Such a semi-solid state characteristic with highly dense random-packed structure may be of significance and could be employed for fabricating new-structure materials, such as with nano-grained or bimodal microstructure, by semi-solid forming from multicomponent alloy systems having a high melting point. This could break through the bottleneck of current semi-solid forming, i.e. producing coarse-grained microstructure from alloys with low melting point and improve its capability for processing alloys with a high melting temperature and for forming novel microstructure as well.
In this work, based on the aforementioned assumption, a material forming method coupling sintering nanocomposite powder with subsequent semi-solid treatment induced by eutectic transformation, referred to as semi-solid sintering, was introduced to fabricate bimodal microstructure in a Ti62Nb12.2Fe13.6Co6.4Al5.8 alloy engineered for both high strength and large ductility. The as-fabricated bimodal microstructure is different from those reported so far, as examples in refs 4, 5, 6, 7, 8, 9, 10, 11, 12, 13. The novel idea is expected to give some insight into fabricating nanostructured metallic alloys having high melting point for high-performance structural applications.
Results and Discussion
Figure 1a shows a high-resolution TEM image and the Fourier-transformed images for the square area and ellipse area of the 70 h-milled Ti62Nb12.2Fe13.6Co6.4Al5.8 powder, i.e. the starting powder used for semi-solid sintering. As seen from Fig. 1a, the 70-milled powder consists mainly of nano-sized β-Ti surrounded by glassy matrix. Its glassy nature is further confirmed by the clear endothermic glass-transition event (at 420 °C) and the strong exothermic crystallization peak (at 490 °C) on the DSC curve of the 70 h-milled powder (Fig. 1b). Two evident endothermic peaks are observed at temperatures of 1125 °C and 1180 °C respectively for the 70 h-milled Ti62Nb12.2Fe13.6Co6.4Al5.8 nanocomposite powder, confirming that there exists a semi-solid interval between 1080 °C and 1200 °C for the Ti62Nb12.2Fe13.6Co6.4Al5.8 alloy.
Figure 2a shows the SEM microstructure of the semi-solid sintered Ti62Nb12.2Fe13.6Co6.4Al5.8 alloy at 1100 °C. Interestingly, the sample consists of a lath-shaped (CoFe)Ti2 twins with a size scale of several tens of microns dispersed in a complicated matrix (Fig. 2a). Detailed TEM analysis (Fig. 2b) of the matrix proves a microstructure of equiaxed TiFe particles with a grain size of 80–120 nm surrounded by β-Ti phase. The corresponding selected-area diffraction (SAD) pattern taken along the [111] zone axis for both β-Ti and TiFe (the inset in Fig. 2b) confirms that the TiFe particle has a bcc CsCl-type structure with a lattice parameter of 0.2998 nm, which is close to that of bcc β-Ti phase (0.3205 nm). The (CoFe)Ti2 twins display an inter-lath spacing of 500–1000 nm (Fig. 2c). The average chemical compositions of the (CoFe)Ti2, TiFe and β-Ti phases determined by EDX are Ti62.02Nb2.77Fe17.40Co17.38Al2.41, Ti58.17Nb4.78Fe31.19Co4.75Al4.78 and Ti64.92Nb25.85Fe4.47Co0.32Al4.43, respectively. In this case, the obtained bimodal microstructure, i.e. the coexistence of nanostructured matrix and micron-sized (CoFe)Ti2 twins, is different from those in the samples fabricated by thermo-mechanical treatment, powder consolidation, recrystallization method, or rapid solidification4,5,6,7,8,9,10,11,12,13. In contrast, the sample sintered at 950 °C, not undergoing semi-solid treatment, is composed of equiaxed face-centered cubic (fcc) (CoFe)Ti2 and bcc TiFe phases with grain sizes of 200–400 nm embedded into equiaxed β-Ti matrix with a grain size of 400–600 nm (Fig. 2d). This equiaxed microstructure is similar to that in titanium alloys by solid-phase sintering of nanocomposite powders in our previous works19,20,21,22.
In order to elaborate the formation mechanism of the bimodal microstructure in titanium alloys during semi-solid sintering, the microstructure evolution in the course of the whole sintering is schematically presented in Fig. 3. As seen from the recorded shrinkage displacement of the punch and the measured temperature as a function of the sintering time (Fig. 3b), the semi-solid processing can be basically divided into four stages. At stage I (temperature below ~490 °C), there is no significant increase in the punch displacement, implying that the rearrangement of powder particles dominates the densification process23. At stage II (temperature ranging 490-1080 °C), the punch displacement rapidly increases first and then stabilizes at a temperature threshold of 720 °C. Below 720 °C, the increase in punch displacement is attributed to that the TiFe and (CoFe)Ti2 phases begin to nucleate and grow from glassy matrix or supersaturated β-Ti phase in sintered nanocomposite powder, leading to a rapid densification21. Above 720 °C, the densification process has completed but grain growth of the three constituent phases (i.e. β-Ti, TiFe and (CoFe)Ti2) continues until forming liquid phase. At stage III (temperature locating at semi-solid temperature interval), the punch displacement displays an instantaneous increase around 1080 °C, indicating the formation of liquid phase induced by the eutectic transformation between the β-Ti and TiFe. This is in good agreement with the onset melting temperature (~1080 °C) on the DSC curve (Fig. 1b) of the as-milled Ti62Nb12.2Fe13.6Co6.4Al5.8 nanocomposite powder. It should be noted that the sintering pressure is relieved immediately once liquid phase forms. Before depressurization, the deformation effect resulting from sintering pressure leads to the formation of fcc (CoFe)Ti2 twins (Fig. 2c). Afterwards, the semi-solid state containing the as-formed liquid phase and remaining solid (CoFe)Ti2 twins is holding at constant 1100 °C under pressure relief. Finally, at stage IV, the as-formed liquid phase is solidified to form the nanostructured matrix at a cooling rate of 400 °C/min (~6.6 K/s) (Fig. 3b), which is far below the magnitude order of the cooling rate (about 100 ~ 1000 K/s) for forming bimodal nanostructure-dendrite titanium alloys by rapid solidification in a water-cooled copper mould7,8,9,10,11,12,13. The reason of forming such a bimodal microstructure composed of nanostructured matrix and micro-sized (CoFe)Ti2 twins in the Ti62Nb12.2Fe13.6Co6.4Al5.8 alloy is mainly ascribed to the highly dense random-packed structure of the remaining liquid in the multicomponent TiNbFeCoAl alloy system. It is well known that a multicomponent glass forming alloy usually has more than three kinds of constituent elements with large atomic size ratios and negative heats of mixing17,24. This can induce a highly dense random-packed structure in the liquid from technological and chemical points of view17,24. Moreover, glass forming ability or degree of dense random packed structure for a multicomponent alloy can be further enhanced by proper adding or modifying elements24. The two aspects are contributed to the formation of the solidified nanostructured matrix from the remaining liquid in the present modified multicomponent TiNbFeCoAl alloy by the addition of refractory element Nb7,8,9. In a word, the formation mechanism of the bimodal microstructure in this work is reversible to that in rapid solidification7,8,9,10,11,12,13. Compared to the formation of bimodal microstructure by rapid solidification, the similar feature is the preferential formation of micron-sized solid microstructure under semi-solid state and the subsequent formation of nanostructured matrix by solidifying the remaining liquid phase.
Theoretically and experimentally, forming liquid phase in the semi-solid forming in this work can be explained based on the eutectic transformation between the β-Ti and TiFe phases. According to the Fe-Ti and Co-Ti binary phase diagrams16, there exist two eutectic reactions at 1085 °C for bcc TiFe and bcc β-Ti and at 1020 °C for fcc CoTi2 and bcc β-Ti, respectively, to transform into liquid phase. Two melting endothermic peaks with peak temperatures of 1125 °C and 1180 °C respectively are distinctly observed on the DSC curve (Fig. 1b) for the as-milled Ti62Nb12.2Fe13.6Co6.4Al5.8 powder. This confirms the existence of a semi-solid state locating between 1080 °C and 1200 °C in the Ti62Nb12.2Fe13.6Co6.4Al5.8 alloy. The theoretical eutectic temperature of 1085 °C for bcc TiFe and bcc β-Ti is well coincident with the onset melting temperature of 1080 °C obtained from the DSC analysis (Fig. 1b) and the exact temperature of instantaneous increase in the punch displacement during sintering process (Fig. 3). This proves that the formation of liquid phase may be attributed to the eutectic transformation between the β-Ti and TiFe phases. In this case, the sample sintered at 950 °C has three phases, i.e. fcc (CoFe)Ti2, bcc TiFe and bcc β-Ti. Note that the (CoFe)Ti2 is a solid solution of Fe atoms substituting for Co positions in fcc CoTi2 compound. The solution of Fe atoms may enhance largely the eutectic transformation temperature of the fcc (CoFe)Ti2 and bcc β-Ti10. Consequently, the bcc TiFe and bcc β-Ti react preferentially into liquid phase and the fcc (CoFe)Ti2 remains solid state and grows from ultrafine grains (Fig. 2d) into micron-sized twins (Fig. 2a,c). The twin structure, usually formed and remained by deformation effect in an fcc solid phase25, again proves the preferential eutectic transformation between the β-Ti and TiFe.
In order to further elaborate the formation mechanism of the present novel bimodal microstructure, the Ti62Nb12.2Fe13.6Co6.4Al5.8 alloy was prepared by rapid solidification in a water-cooled copper mould for comparison. Obviously, the as-solidified alloy consists of only β-Ti phase and TiFe phase. It displays a typical bimodal microstructure of a primary micron-sized β-Ti phase (in a dark color) dispersed in a nanostructured eutectic matrix with β-Ti phase and TiFe phase (in a light color) (Fig. S1). This once again confirms that the formation of the semi-solid state in the present work is induced by the eutectic transformation between the β-Ti and TiFe phases rather than that between the β-Ti and (CoFe)Ti2 phases. Besides, the semi-solid state induced by preferential eutectic transformation between the β-Ti and TiFe rather than by that between the β-Ti and (CoFe)Ti2 can also be supported by the additional experiments carried out in Ti66Nb13Fe8Co6.8Al6.2 alloy with lower Fe content (Figs S2–5 in the supplementary information compared with the present Ti62Nb12.2Fe13.6Co6.4Al5.8 alloy). As seen from Fig. S2, single melting endothermic peak with a peak temperature of 1185 °C in DSC curve, the presence of the same (CoFe)Ti2 twins and β-Ti in sintered Ti66Nb13Fe8Co6.8Al6.2 alloy (Figs S3 and S4) and absence of instantaneous increase in the punch displacement around 1080 °C (Fig. S6) during sintering for the Ti66Nb13Fe8Co6.8Al6.2 powder further confirm that the (CoFe)Ti2 phase is in a solid state at sintering temperature of 1100 °C. As such, the formation of such a liquid phase results from the preferential eutectic transformation between the β-Ti and TiFe in the Ti62Nb12.2Fe13.6Co6.4Al5.8 alloy. From another point of view, if the formation of liquid phase originates from a ternary eutectic transformation of the bcc β-Ti, bcc TiFe and fcc (CoFe)Ti2, it is impossible to obtain the bimodal microstructure in the present case according to the formation mechanism of bimodal microstructure in rapid solidification7,8,9,10,11,12,13. In a word, forming liquid phase in Ti62Nb12.2Fe13.6Co6.4Al5.8 alloy is certainly attributed to the preferential eutectic transformation between the β-Ti and TiFe phases.
Figure 4a presents the compressive engineering stress-strain curve for the semi-solid sintered Ti62Nb12.2Fe13.6Co6.4Al5.8 alloy compared with the sintered sample at 950 °C. All the mechanical properties, i.e. strength and strain in deformation, were averaged by three tests. As seen from Fig. 4a, the equiaxed-grained sample sintered at 950 °C exhibits ultrahigh yield strength of 1850 MPa but limited plastic strain. In contrast, the sample with bimodal microstructure prepared by semi-solid sintering has ultrahigh yield strength of 1790 MPa as well as large plastic strain of 15.5%. In order to compare the mechanical properties of the present samples with those of other types of representative bimodal-microstructure titanium alloys by rapid solidification7,8,9,10,11,12,13, yield strength versus plastic strain are summarized and presented in Fig. 4b. Evidently, the semi-solid sintered samples reported herein exhibit simultaneous high strength and large plastic strain, which are superior to most of as-reported bimodal titanium by rapid solidification. This is ascribed to the collaborative effects of the three constituted phases in the bimodal microstructure under loading12. Profuse dislocations and shear bands formed in the β-Ti regions are blocked and branched and multiplied by the micron-sized (CoFe)Ti2 twins (Fig. 5b,c) and nano-sized TiFe particles (Fig. 5c). This indicates that the deformability of (CoFe)Ti2 phase and TiFe phase is not large. The preferentially formed micro-cracks in the isolated fcc (CoFe)Ti2 twins are separated, hindered and restricted by the surrounded nanostructured matrix (Fig. 5b), causing zigzag crack paths and avoiding shearing-off through the whole sample (Fig. 5a).
In summary, this work has successfully prepared a bimodal microstructure in Ti62Nb12.2Fe13.6Co6.4Al5.8 alloy via a novel approach of semi-solid sintering induced by eutectic transformation. Its high yield strength results from nanostructured matrix and strengthening effect of micron-sized (CoFe)Ti2 twins. The large plasticity is ascribed to the profuse shear bands in nano-sized β-Ti phase and associated block effects by nano-sized TiFe phase. The findings will help guide endeavors to obtain high-performance metallic materials in alloy systems with a high melting point.
Methods
In present experiments, the process started by preparing Ti62Nb12.2Fe13.6Co6.4Al5.8 (at.%) alloy powder from respective element powder by mechanical alloying in a high-energy planetary ball mill (QM-2SP20, apparatus factory of Nanjing University) under a purified argon gas atmosphere. Approximately 3 g of the powder was removed from the mill-vial every 10 h for X-ray diffraction (XRD) examination (D/MAX-2500/PC, Rigaku Corp., Tokyo, Japan) until the formation of nanocomposite structure with an amorphous matrix surrounding β-Ti nanocrystals after 70 h milling. Then, differential scanning calorimetry (DSC, Netzsch STA 409 C) was employed to determine the semi-solid temperature interval of the as-milled powder. Afterwards, the as-milled powder was semi-solid sintered by the following two-step method under continuous heating to semi-solid interval (1100 °C) under an argon atmosphere by a Dr. Sintering SPS-825 system. In the first step, samples were heated from room temperature to 1050 °C at a heating rate is 100 °C/min and the sintering pressure was 50 MPa. In the second one, when the samples were heated to 1100 °C from 1050 °C at 50 °C/min under 50 MPa, the sintering pressure was relieved immediately and the sample were hold at 1100 °C for 5 min without pressure. For comparison, additional Ti62Nb12.2Fe13.6Co6.4Al5.8 specimens were sintered at 950 °C using the same parameters. The detailed experimental procedures can be seen in ref. 19,20.
Instantaneous values of sintering parameters, such as temperature, punch displacement and time, were recorded every 2 seconds by the attached software. The cooling rate of the semi-solid sintered alloy was determined by calculating the slope of the temperature curve of the as-sintered alloy during the cooling process. All sintered bulk samples had a cylindrical shape with a dimension of Ф20 × 10 mm. A Philips XL-30 FEG scanning electron microscopy (SEM; Amsterdam, The Netherlands) and a Tecnai G2 F30 field emission gun transmission electron microscopy (TEM; FEI, Eindhoven, The Netherlands) coupled with energy dispersive X-ray (EDX) analysis were used for microstructure investigation. In order to evaluate the mechanical properties under compression for comparison with the reference alloys, cylindrical specimens of 3 mm in diameter and 6 mm in length were tested in a universal testing machine (MTS testing system) under quasistatic loading at a strain rate of 5 × 10−4 s−1.
Additional Information
How to cite this article: Liu, L. H. et al. A new insight into high-strength Ti62Nb12.2Fe13.6Co6.4Al5.8 alloys with bimodal microstructure fabricated by semi-solid sintering. Sci. Rep. 6, 23467; doi: 10.1038/srep23467 (2016).
References
Hemker, K. J. Understanding how nanocrystalline metals deform. Science 304, 221–222 (2004).
Ma, E. Eight routes to improve the tensile ductility of bulk nanostructured metals and alloys. JOM 58, 49–53 (2006).
Gianola, D. S. et al. Stress-assisted discontinuous grain growth and its effect on the deformation behavior of nanocrystalline aluminum thin films. Acta. Mater. 54, 2253–2263 (2006).
Wang, Y. M., Chen, M. W., Zhou, F. H. & Ma, E. High tensile ductility in a nanostructured metal. Nature 419, 912–915 (2002).
Witkin, D., Lee, Z., Rodriguez, R., Nutt, S. & Lavernia, E. Al-Mg alloy engineered with bimodal grain size for high strength and increased ductility. Scripta Mater. 49, 297–302 (2003).
Srinivasarao, B., Oh-ishi, K., Ohkubo, T., Mukai, T. & Hono, K. Synthesis of high-strength bimodally grained iron by mechanical alloying and spark plasma sintering. Scripta Mater. 58, 759–762 (2008).
He, G., Eckert, J., Löser, W. & Schultz, L. Novel Ti-base nanostructure-dendrite composite with enhanced plasticity. Nat. Mater. 2, 33–37 (2003).
He, G., Eckert, J. & Löser, W. Composition dependence of the microstructure and the mechanical properties of nano/ultrafine-structured Ti-Cu-Ni-Sn-Nb alloys. Acta Mater. 52, 3035–3046 (2004).
Kühn, U. et al. Nanostructured Zr- and Ti-based composite materials with high strength and enhanced plasticity. J. Appl. Phys. 98, 054307 (2005).
Louzguine-Luzgin, D. V., Louzguina-Luzgina, L. V., Kato, H. & Inoue, A. Investigation of Ti–Fe–Co bulk alloys with high strength and enhanced ductility. Acta. Mater. 53, 2009–2017 (2005).
Zhang, L. C., Lu, H. B., Mickel, C. & Eckert, J. Ductile ultrafine-grained Ti-based alloys with high yield strength. Appl. Phys. Lett. 91, 051906 (2007).
Zhang, L. C. et al. High strength Ti-Fe-Sn ultrafine composites with large plasticity. Scripta Mater. 57, 101–104 (2007).
Das, J., Ettingshausen, F. & Eckert, J. Ti-base nanoeutectic-hexagonal structured (D019) dendrite composite. Scripta Mater. 58, 631–634 (2008).
Atkinson, H. V. Modelling the semisolid processing of metallic alloys. Prog. Mater. Sci. 50, 341–412 (2005).
Fan, Z. Semisolid metal processing. Int. Mater. Rev. 47, 49–85 (2002).
Nagasaki, S. & Hirabayashi, M. Binary Alloy Phase diagrams, AGNE Gijutsu Center, Co., Ltd., Tokyo, Japan, 2002.
Inoue, A. Stabilization of metallic supercooled liquid and bulk amorphous alloys. Acta Mater. 48, 279–306 (2000).
Lu, K. Nanocrystalline materials crystallized from amorphous solids: nanocrystallization, structure and properties. Mater. Sci. Eng. R. 16, 161–221 (1996).
Yang, C., Liu, L. H., Cheng, Q. R., You, D. D. & Li, Y. Y. Equiaxed grained structure: A structure in titanium alloys with higher compressive mechanical properties. Mater. Sci. Eng. A. 580, 397–405 (2013).
Liu, L. H. et al. Equiaxed Ti-based composites with high strength and large plasticity prepared by sintering and crystallizing amorphous powder. Mater. Sci. Eng. A. 650, 171–182 (2016).
Liu, L. H. et al. Densification mechanism of Ti-based metallic glass powders during spark plasma sintering process. Intermetallics 66, 1–7 (2015).
Liu, L. H. et al. Ultrafine grained Ti-based composites with ultrahigh strength and ductility achieved by equiaxing microstructure. Mater. Design 79, 1–5 (2015).
Robertson, I. M. & Schaffer, G. B. Review of densification of titanium based powder systems in press and sinter processing. Powder. Metall. 53, 146–162 (2010).
Wang, W. H. Roles of minor additions in formation and properties of bulk metallic glasses. Prog. Mater. Sci. 52, 540–596 (2007).
Christian, J. W. & Mahajan, S. Deformation twinning. Prog. Mater. Sci. 39, 1–157 (1995).
Acknowledgements
This work was supported by the National Natural Science Foundation of China (No. 51574128), the Guangdong Natural Science Foundation for Research Team (No. 2015A030312003), the Guangdong Natural Science Foundation (No. S2013010012147) and Australian Research Council Discovery Project (DP110101653) and (DP130103592).
Author information
Authors and Affiliations
Contributions
C.Y. and Y.Y.L. conceived the study. L.H.L., C.Y. and L.C.Z. wrote the manuscript. L.H.L. conducted the experiments, L.H.L., C.Y., L.M.K., S.G.Q., X.Q.L., W.W.Z., W.P.C., Y.Y.L. and P.J.L. analyzed the data. All authors reviewed the manuscript.
Ethics declarations
Competing interests
The authors declare no competing financial interests.
Electronic supplementary material
Rights and permissions
This work is licensed under a Creative Commons Attribution 4.0 International License. The images or other third party material in this article are included in the article’s Creative Commons license, unless indicated otherwise in the credit line; if the material is not included under the Creative Commons license, users will need to obtain permission from the license holder to reproduce the material. To view a copy of this license, visit http://creativecommons.org/licenses/by/4.0/
About this article
Cite this article
Liu, L., Yang, C., Kang, L. et al. A new insight into high-strength Ti62Nb12.2Fe13.6Co6.4Al5.8 alloys with bimodal microstructure fabricated by semi-solid sintering. Sci Rep 6, 23467 (2016). https://doi.org/10.1038/srep23467
Received:
Accepted:
Published:
DOI: https://doi.org/10.1038/srep23467
This article is cited by
-
Effect of Mechanical Alloying and Sintering Environment on the Crystallographic Evolution, Microstructure, Mechanical and Corrosion Properties of Porous Ti4Al4Co Alloy
Metals and Materials International (2022)
-
Corrosion and Wear Behaviour of Spark Plasma-Sintered NiCrCoAlTiW-Ta Superalloy
Journal of Bio- and Tribo-Corrosion (2020)
-
Microstructures and mechanical properties of in situ TiC–β–Ti–Nb composites with ultrafine grains fabricated by high-pressure sintering
Scientific Reports (2018)
-
Texture evolution and mechanical behavior of commercially pure Ti processed via pulsed electric current treatment
Journal of Materials Science (2016)
Comments
By submitting a comment you agree to abide by our Terms and Community Guidelines. If you find something abusive or that does not comply with our terms or guidelines please flag it as inappropriate.