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METALLURGY dered structures are intrinsically brittle. The gain Multicomponent intermetallic of gigapascal strengths by introducing highdensity IMCs invariably leads to a reduced resistance to fracture. The highly reactive elements, nanoparticles and superb mechanical such as Al in the NijAl intermetallic phase, will also increase the susceptibility of these interbehaviors of complex alloys metallics to moisture-induced environmental embrittlement and further lower their tensile ductility (6,7). Moreover, the microstructural heterogeneity of IMCs tends to introduce a localized T. Yang 1,2, Y. L. Zhao 2, Y. Tong 2, Z. B. Jiao 3, J. Wei 2, J. X. Cai 4, X. D. Han 4, D. Chen 2, stress-strain concentration and trigger microA. Hu2, J. J. Kai 2,K.Lu5, Y. L.iu , C. T. L.iu 1,2 cracks under loading (8). Consequently, the early onset of plastic instability leads to a catastrophic fallure of these materials. Conventional alloy design based on singleprincipal-element alloy systems cannot break through this thorny dilemma, because of the limited abilities for further optimizing alloy chemistries and microstructures. Recently proposed metallurgical design in multi-principal-element alloy systems offers a promising pathway to atleviate these concerns (2,912). Nevertheless, the results obtained so far have been disappointing at ambient temperatures, at which high-strength Department of Material Science and Engineering, Colkge of Soience and Engineering. Cty Unversity of Hong Kong, Hong Kong, China. "Center for Advanced Structural Materials/ Department of Mectarical Engineering, College of Science and Engineering, Cty Unvesity of Hong Kong, Hong Kong. China. Department of Mechanical Engineering, Hsng Kong Polytectric Univessity, Hong Kong. China "Irstitule of Mcrostructure and Properties of Mdvanced Masteriass, Being University of Technology, Being 100124, Chins Sherearg National Laboratory for Materiass Science, Irstitute of Metal Arsearch, Chinese Academy of Sciences, Shenymg 110016 . China. Central South University, Changsha 400083 , Hunan, Ohins. Fig. 1. Conceptual design and microstructural characterizations of the MCINPS alloys. (A) Schematic of the design concept of the MCINPS alloys. MCM, multicomponent matrix. (B) Scanning electron microscopy units. (E) TEM image of the AJTTi7 aloy showing the nanostructured (SEM) image of the AlJTi7 alloy exhibiting the typical equiaxed grain morphology. The inset shows the corresponding SAED pattern. (F) Repstructures. (C) SEM image of the Al7Ti7 alloy revealing the uniform resertative high-resolution TEM image confirming the interfacial coherency. A B Fig. 2. Spatial morphology and multicomponent nature of the MCINPs. (A) 3D reconstruction map of an APT needle tip confirming the nanocomposited microstructure of the AITTi7 alloy. (B) High-resolution atom maps showing the atomistic distribution within the Ll2 MCINP of the AIJTi7 alloy. (C) Proximity histogram across the matrix and nanoparticles revealing the multicomponent nature of the MCINPs of the AIZTi7 alloy. (D) Ordering crystallographic structure and site occupancy of the L12 MCINP by density functional theory (DFT) calculations of the AITi7 alloy. ates necking in the AlsTi6 alloy upon further straining. The Al7Ti7 alloy, by contrast, has a markedly different deformation behavior as the work hardening continues at larger strains The instantaneous work-hardening exponent n in this stage shows a linear increase with a high value of 0.43 (Fig. 4B ), which implies the onset of an additional deformation mode, enabling an extended uniform deformation to be sustained. With the aim of deciphering the origin of the unusual work-hardening behavior of the Al7I7 alloy, we carefully investigated the dynamic evolution of deformation substructures at different strains with TEM (Fig. 4C). At the true strain of 10%, the deformation was dominated by the planar slip of dislocations along the {111} primary slip planes, similar to that observed in most fce-type alloys (23-25). As the true strain increases to 22%, we observed well-developed HDDWs along the primary slip systeme The formation of these directional dislocation substructures (dislocation arrays and HDDWs) produced a long-range back stress that makes dislocations in the interwall space difficult to move through them, leading to an increased work-hardening response (26-28). Moreover, we observed wavy slips in the interwall space, indicating that the dislocation cross-slip is effectively activated at this stage. The intensive polyslips of dislocations are helpful for relieving the stress concentration on the {111} primary slip planes. Meanwhile, the progressive accumulation of these in-directional dislocations and their mutual interactions produced a pronounced forest dislocation hardening, le, the short-range effective stress hardening (29-32). We conducted tensile boad-unload-reload tests to further quantify the Fig. 3. Exceptional strength-ductility combination achieved in the MCINPS alloys at ambient temperature. (A) Engineering stress-strain curves of the MCINPS aloys compared with the FeCoNi sponses and associated flow stress partitioning base alloy (12), showing a significant increase of strength without ductility reduction. The AlTti7 behaviors (ffg. S14). We observed a large increase alloy exhibits ductile dimpled structures without macroscopic necking. (B) Yield strength versus the in short-range effective stress, the strengthenproduct of strergth and ductility of the MCINPS alloys compared with those of other high-performing ing contribution of which is almost identical to materials (2,4,5,8,11,13,14,19,21,22). that of the long-range back stress hardening. Therefore, the high work hardening of the AlzIM Increased plastic deformation allows us to not only effectively impede the dis11. B. Cludovatz of al., Soience 345 . 1153-1158 (2014). 41. D. Hughes, Acto Motat Marer, 41, 14z location motion for strengthening but also increase the damage tolerance and dislocation storage of 12. 2. Wu. H. Bei, id. 42. I. Gutierrez-Umutia, D. Aasbe, Scr. Ma 43. P. Hackon, Scr Motal. 17, 199-202 ( the alloys. 13. W. H. Lue at al. Acts Mater. 116. 332-342 (2016). 44. 1. Hung, E. Eray II, Acta Mobalt 3r, 46. A. Chba, S. Hanada, 5 . Watanabe, It In conclusion, we proposed an innokative alate-113 (12982) loy design strategy by engineering high-density MCINPS in camplex alloy systems to achieve sa15. Materaks and methods are avallable as applementary materiak. 45. C. Meng, 1. Oin, Z. Hu, 1 Intry. So. Ter 47. D. Faynac, Slloock, Mot. Sol. 14 , 1. perb mechanical properties at ambient temper- 18. F. C. Reed, C. M. F. Rae, in Fhysical Motilury of the 43. C. T. Liu. Int. Mofas Riv. 29, 169-194 ature. We demonstrated experimentally that the 19. B. Eeddes, H. Leon, X. Hung, Superalloys aloying and MCINPS alloys are simultaneously ultrastrong performance. (Asm hitemational, zoto). 49. C. T. Uu C. L White, Mas' Proconding and ductile, with no strength-ductility trade-off 20. Y. L. Ustinovahkov, L. N. Shabanova. N. Y. Lomova. 1. Adk Meresc Res. 8. 27-32 (2013). We thank L. H. Wang. Z. P. U, and L. B. H and plastic instability. This alloy design strategy can also be fessibly applied to many other alloy systems, such as nanostructured alloys, steels, 1141-1144 (2009). superalloys, and also HEAs, to achieve desired 23. B. Cludovatz on al., Nat. Commun. 7, aDso2 (2006). Government through the CFF tunds with and enhanced properties for specific applications. The resulting new-generation complex alloys could 25. B. Ma, C. L, 1 Zneng, Y. Song, Y. Han, Mator. Des 92, 313-321 (2016). lead to superior structaral properties, which are of both great fundamental and applied importance 26. X. Hu ef al, Motal Mater. Tars. A Phys. Motal. Maxar. Sol. 48 Nofonal Natural Solenoe Foundation (no for advanced engineering applications involving 1. Acad. Sol. US.A. 112, 14501-14505 (2005). and Y.T. prepared and characterbed the 2 automobiles, bullet trains, cryogenic devices, and aircraft and aeronautic systems. 30. C. Keler, M. Mrgulies, I. Hademtamouche, L. Gullot, Itafer KL,XDH, ZB., YL, and 1KK andyazr REFERENCES AND NOTES 31. Y. Tang of al, Metak (Easel) 8, 444 (2023). 1. R. Q. Finchic, Nat. Matec 10, 8178222 (2001). 32. A. Vattre, B. Devincre, A. Foos, Intermetalics 17, 989-994 manuscript. Competing interests None and materials avalability: All data are 2 Z. LI K. G. Pradesp. Y. Deng. D. Rowhe, C. C. Taen, Nature (2009). O. M. Stocks, Y. Zheng, Acto Murer. 134. 334-345 or the supplementary materiak. 3. R. Lie, Z \& Zhang, L. L Li, X. H. An. Z. F. Zhang, Sci. fiep. 5, 33. 5 . Inao, 9E80 (2005). 34. X. Mie, SUPPLEMENTARY MATERIALS 4. S. H. Kim, H. Kum, N. . . Km, Nature 518, 77-79 (2015). (1985). wwscienoem2g. org/content/352/6417/