Synergetic strength-ductility enhancement of ultra-thin W wire by La oxide nanoprecipitates induced pinning effect

Synergetic strength-ductility enhancement of ultra-thin W wire by La oxide nanoprecipitates induced pinning effect | Research Square window.SnipcartSettings = { analytics: { enabled: false } }; (function() { var accessVector = localStorage.getItem('access_vector') || ''; window.dataLayer = window.dataLayer || []; if (accessVector) { window.dataLayer.push({ user: { profile: { profileInfo: { snid: accessVector } } } }); } })(); (function(w,d,s,l,i){w[l]=w[l]||[];w[l].push({'gtm.start':new Date().getTime(),event:'gtm.js'});var f=d.getElementsByTagName(s)[0],j=d.createElement(s),dl=l!='dataLayer'?'&l='+l:'';j.async=true;j.src='https://www.googletagmanager.com/gtm.js?id='+i+dl;f.parentNode.insertBefore(j,f);})(window,document,'script','dataLayer','GTM-K279D39R'); Browse Preprints In Review Journals COVID-19 Preprints AJE Video Bytes Research Tools Research Promotion AJE Professional Editing AJE Rubriq About Preprint Platform In Review Editorial Policies Our Team Advisory Board Help Center Sign In Submit a Preprint Cite Share Download PDF Article Synergetic strength-ductility enhancement of ultra-thin W wire by La oxide nanoprecipitates induced pinning effect Tao Zhang This is a preprint; it has not been peer reviewed by a journal. https://doi.org/ 10.21203/rs.3.rs-4766443/v1 This work is licensed under a CC BY 4.0 License Status: Posted Version 1 posted You are reading this latest preprint version Abstract Ultra-thin W wire is one of the few tools that can cut precious hard materials, including wafers, silicon, and sapphire. Reducing the diameter of tungsten wire by increasing the strength of W wire is the only method to achieve lower material waste and higher precision. Here, we report an ultra-thin La-doped W wire produced by the ice bath assisted non-slip drawing, with a diameter of 38.0 μm and a continuous length exceeding 50 km, exhibiting a tensile strength up to 6.92 GPa with an elongation of 4.2%. Statistical analysis-assisted atomic resolution imaging and element distribution mapping and molecular dynamics (MD) simulations revealed that the hexagonal close-packed (hcp) La oxide precipitates pin at the grain boundaries and form a coherent interface with the body-centered cubic (bcc) W matrix, inducing the nano twins and local hcp region in bcc W matrix, which originates lattice distortion and dislocations, and altered the plastic deformation mechanism of W. The coherent W-La oxide interface enhances the plastic deformation of grain boundaries and effectively elevates the uniform deformation, thereby simultaneously enhancing the strength and ductility. The ice bath assisted non-slip drawing is applicable to diverse metal wires and is of high potential for scalable and industrial applications. Physical sciences/Materials science/Structural materials/Mechanical properties Physical sciences/Materials science/Structural materials/Metals and alloys Figures Figure 1 Figure 2 Figure 3 Figure 4 Introduction Ultra-thin W wires are of great importance as saw wires in precision cutting of hard materials 1 . They also have extensive utilities in other purposes, such as plasma-facing materials 2 , 3 , 4 , medical radiation protection 5 , fine circuitry printing 6 , and cathode materials in magnetrons 7 . These applications leverage the unique properties of tungsten wires: ultra-thin diameter, high strength, excellent heat and corrosion resistance 8 . Utilized as the saw wires, if the ultra-thin W wires have a much higher tensile strength, the added benefits are much higher flexibility, a significantly larger cutting force, and considerably smaller instability of the cutting effect 9 . Typically, we use a series of cone pulleys mounted in a slip-drawing machine under heating and lubrication conditions to draw W wire. Under traditional conditions, the grain size tends to increase, nano twins (coupled with dislocations) are prone to annihilation, and the nanoprecipitates coarsen rapidly in medium and high temperatures due to the combined heat generated from external sources and dynamic friction, weakening the alloys 10 . As a result, the conventional heating assisted slip-drawing method fails to produce ultra-high strength W wires because of the thermal effects during fabrication, limiting the development of ultra-thin W wires. Traditional methods, including twin crystals induction 11 , 12 , precipitate/solution strengthening 13 , 14 , and grain refinement 15 , 16 , are widely employed to augment and improve the alloy strength and toughness. Twin boundaries can improve the strength and plasticity of the alloy without compromising the fracture resistance by impeding and permitting incoming dislocations 17 , 18 . Lu et al. embedded the high-density thin twin boundaries in individual grains of copper, improving tensile strength by 10 times relative to the conventional coarse-grained polycrystalline counterpart 19 . High twin boundary (TB) densities in metals and alloys are achievable under certain conditions 20 , such as electrodeposition 21 , sputtering 22 , and severe plastic deformation 23 , 24 . While most of the manufacturing methods are accomplished in face-centered cubic (fcc) metals 25 , mainly in Cu 26 and steel 27 , few are in hcp metals like Ti 28 . Nevertheless, due to high stacking fault energy (SFE) 11 , 13 , 29 , 30 , bcc crystal structured metals exhibit low twinning dynamics 31 , deformation twins in most bcc metals are unstable and undergo spontaneous detwinning upon unloading 32 . Cost-effectively introducing stabilized nano-twinned structures into bcc metals has always been challenging. While solute atoms can engineer nano-twinned structures, segregation can supply a pinning effect for nano twin boundaries 33 , thereby it's feasible to induce nano twins by segregation in bcc metals. Chen and Yang et al. found that in bcc W electrode materials, La 2 O 3 particles, acting as a dispersion-strengthening phase, have a clear phase interface with the W matrix 34 , which was further identified as semi-coherent or incoherent interfacial relationship 35 , exerting a substantially positive effect on the mechanical properties. Herein, we developed an ultra-thin La-doped W wire by introducing the La oxide particles into the W matrix, which forms the nanoprecipitates at the W grain boundaries. Transmission electron microscopy (TEM) results demonstrate that the hcp La oxide is uniformly pinned at the W grain boundaries, forming a coherent interface with the bcc W matrix. As molecular dynamics (MD) simulation reveals, plastic deformations occur at the region of La oxide during the deformation process, which significantly enhances the plastic deformation of grain boundaries and effectively elevates the uniform deformation, thereby promoting the strength and plasticity simultaneously. Moreover, the addition of La oxide induces the nano-twinned structures in W(La) solid solutions by reducing the SFE of W on the basis of the density-functional theory (DFT) calculations, thus hindering the dislocations movement, which further improves the tensile strength of W wires. In the manufacturing process, we used a non-slip drawing technique with an ice bath to enhance mechanical properties and circumvent the heat-induced coarsening of nanoprecipitates and twin annihilating. Cold drawing refines the grain size to below 23 nm, which is due to the formation of high-angle grain boundaries induced by intensive dislocations rearrangement 36 , 37 , 38 . The resulting ultra-thin W wire reached a peak tensile strength of 6.92 GPa, an elongation rate of 4.2%, and a continuous length surpassing 50 km. The synergy of nano twin boundaries, nanoprecipitates and ultrafine grains account for the La-doped W wire’s exceptionally high mechanical properties. The fabrication method can be applied to various ultra-thin metal wire manufacturing and shows great potential for industrial production. Results and discussion The microstructure analysis of the La-doped W wire Figure 1 a illustrates the schematic of the non-slip drawing mechanism. With an initial diameter of 2.0 mm, we used the non-slip equipment to draw the raw La-doped W wire under ice bath conditions. As opposed to the traditional cone trolley slipping process, by employing a rubber-wrapped capstan to provide static friction, we maintained a constant grip on the wire (no slip friction), effectively cutting heat generation to a great extent. The concurrent use of an ice bath lowers the wire temperature, which helps preserve the fine grain size, twins, and high quantities of dislocations during the dynamic drawing process. The enhanced strength of W wires allows for further reduction of wire diameter. Figure 1 b-e displays the drawing length, diameter distribution uniformity, wire diameter, and mechanical strength of the La-doped W wire. Figure 1 b compares a reel winding 50 km of La-doped W wire with an empty reel. Figure 1 c depicts the diameter tolerance of the La-doped W wire across a length of 50 km, demonstrating exceptional uniformity with a tolerance of approximately 38.0 ± 0.1% µm. The high uniformity suggests that it is highly feasible to produce the La-doped W wire at long lengths with narrow diameter distribution, and the non-slip drawing method is also highly suitable for industrial applications. Figure 1 d presents the scanning electron microscopy (SEM) image of an ultra-thin La-doped W wire alongside a human hair. With a remarkably smooth surface, the W wire’s diameter is 38.0 µm, approximately half the diameter of a human hair. Figure 1 e testifies the strength of a single 38.0 µm diameter La-doped W wire, capable of lifting a 500 g weight (Supplementary Movie 1). To explore the effects of La element and the drawing process on microstructure, we performed the focused ion beam (FIB) etching on the cross sections of La-doped and pure W wires, both with a diameter of 38.0 µm (see inset in Fig. 1 f). We employed the two TEM images from La-doped and pure W wires separately to compare the microstructures of post-etching specimens. Figure 1 f reveals the lath-shaped grain morphology with a grain size of approximately 21.5 nm in the La-doped W sample. Figure 1 i shows the high-resolution TEM (HRTEM) image of nanoprecipitates uniformly distributed at the grain boundaries, with a diameter of about 25.8 nm. Supplementary Fig. 1 shows an enlarged view of the precipitate in the grain boundary. We further analyzed the chemical composition of precipitates by the energy dispersive X-ray spectrometer (EDS) (Fig. 1 g), revealing the W-La-O composition of the precipitate. The content of La in the precipitates is as high as 30.81% (Fig. 1 h), indicating that La oxides mainly distribute at the grain boundaries in the precipitate form. Figure 1 j-k depicts the average dimensions of the La oxide precipitates and the grain sizes statistically. The precipitates and the grains sizes exhibit a narrow size distribution, with the nanoprecipitates between 0.4–0.9 nm and grains between 11–23 nm. The refined and axially oriented grains, coupled with enormous amounts of dislocations from the extreme plastic deformation under the cold drawing, contribute to enhanced tensile strength 39 . We prepared a pure W wire under identical conditions to clarify the effect of the La element on the microstructure and grain size. The aberration-corrected scanning TEM (STEM) image of pure W wires shows no precipitates at grain boundaries (Fig. 1 l). The statistical columnar graph exhibits that the average grain size of pure W wire ranges from 15 to 35 nm (Fig. 1 m), which is significantly larger than the La-doped W wire but still at the nanometer size level. The above results indicate that the non-slip ice bath drawing process restrains grain growth due to the smaller heat generation during the drawing process. The La-doped and pure W wires, processed using the same non-slip ice bath drawing technique, possess the nano-crystalline structures. The nano crystallines serve the purpose of accumulating geometrically necessary dislocations (GND), increasing the total dislocations, and inducing back stress 40 in the wire crystals, thus enhanced the tensile strength and augmented the elongation through strain hardening. Nano twins and stacking fault structures in bcc metals The SFE is an important intrinsic parameter of metal materials, which influences the deformation mechanism and mechanical properties of metal materials. The SFE is closely related to structural phase transformations, especially in severe plastic deformation. The change of SFE plays a decisive role in the metal deformation mechanism and grain refinement mechanism 41 . Typically, nano twins and stacking fault (SF) structures facilitate the plastic deformation in low SFE fcc metals, thus inducing high strength of metallic materials by obstructing mobile dislocations 19 , 42 , 43 , 44 , 45 , storing dislocations during plastic deformation 46 , and migrating under stress 47 , 48 , 49 . To further investigate the impact of La addition on the W crystal structure, we conducted first-principle calculations based on DFT models 50 to compare the SFE of bcc pure W and W-La alloys (Fig. 2 a). We reveal that the SFE of the La-W alloys is 36.2% lower than that of pure W, demonstrating that adding La oxides reduces the SFE of bcc crystal structure W greatly, thereby making the binary La-W alloys more prone to induce twins and SF structure. To verify the results of the DFT calculation, we analyzed the FIB samples of La-doped W wire and the pure W wire by TEM. Figure 2 b shows a bright-field TEM image of the La-doped W wire, revealing large quantities of nano-twinned structures exist within the bcc matrix. The TEM observation aligns with the simulation calculations on the SFE, as adding La reduces the SFE of W crystal structure in bcc metals, culminating in forming more nano-twinned structures under stress. Figure 2 c presents an enlarged view of twins from Fig. 2 b, and the inset in Fig. 2 c displays the HRTEM image with an interlayer width of 1.41 nm. Figure 2 d illustrates the high-angle annular dark-field scanning transmission electron microscopy (HAADF-STEM) image of a TB, highlighted by a yellow solid line, where the lattice spacings on either side of the line are both 0.13 nm, matching the (211) plane and correlate with the standard La 2 O 3 (JCPDS No: 05-0602), the inset image shows the corresponding selected fast Fourier transform (FFT), taken along [315//135] zone axis (ZA) at the yellow solid line area. The above observation confirms that the twinned structure originates in the La oxide precipitates area. Figure 2 e-f shows the HRTEM images of typical dislocated SF regions within the La oxide precipitates. The red dotted lines label the phase boundary between the matrix and the La oxide precipitate, and the yellow dotted lines denote the SF structures. Labeled by white lines, we measured one SF structure having a width of 2.08 nm and a length of 12.46 nm. The SFs present within the La oxide precipitate regions suggest that adding La facilitates the SF induction in precipitates. In contrast, despite having high intrinsic strength due to a nano-crystalline structure, the pure W wire exhibits no twinned structures in the TEM images, agreeing with the simulation predictions. Based on the above analysis, we confirm that adding La lowers the SFE and introduces twin and SF structures to bolster the strength of ultra-fine La-doped W wires. Pinning effect in the La oxide precipitated region Labeled in a yellow solid line, Fig. 2 g illustrates the HAADF-STEM image of the phase interface between the W-matrix and the La oxide precipitate. The lattice spacings on the W-matrix side are 0.08 nm and 0.11 nm, corresponding to the (400) and (220) planes, respectively, in agreement with standard W (JCPDS No: 04-0806). On the La oxide precipitate side, the lattice spacing is 0.13 nm, representing and matching the (211) plane of standard La 2 O 3 (JCPDS No: 05-0602). The inset shows an FFT pattern along the [315] ZA within the La oxide precipitate region. We prove that the ordered La oxide precipitates pinning the phase and twin boundaries. Figure 2 h-i are the HAADF-STEM images of the La oxide precipitate outlined by the red-colored dotted circles, with widths of 0.94 nm and 1.77 nm, respectively. Both have FFT patterns along the [315] ZA from the circled areas. We also captured the partial dislocations existing in precipitates, marked with red ‘T’ symbols, presenting that La oxide precipitates are prone to induce dislocations during the deformation process due to the pinning effect. The strain field surrounding the La oxide precipitate is mapped out using the geometrical phase analysis (GPA) approach. Figure 2 j shows the HRTEM image of a La oxide precipitate at a grain boundary with GPA strain maps on the ε xx (Fig. 2 k) and ε xy (Fig. 2 l), respectively. The GPA maps display the dislocations marked with yellow arrows at the La oxide precipitate, revealing the impact of the lattice distortion. The severe lattice distortion improves the stiffness and strength of the saw wires greatly, which are also beneficial to the overall tensile-bearing capability. The distortion indicates that a significant lattice strain exists near the La oxide precipitates, leading to elevated energy levels. La oxide doping stabilizes the grain boundaries by the pinning effect, thus stabilizing grain boundary segregation thermodynamically, reducing the grain boundary energy, and lessening the instability of nanocrystal metals 51 . The in-situ TEM movie of the La-doped W wire’s drawing fracture process (Supplementary Movie 2) and the fracture microstructure in STEM image (Supplementary Fig. 2) after drawing further confirm the La oxide precipitate’s pinning effect. The schematic illustration (Supplementary Fig. 3) shows the mechanisms of the pinning effect under stress. The pure W cracks along the nanograin under stress, while the La oxide in the grain boundary can absorb the stress energy and plays the role of pinning effect to prevent the fracture, thereby increasing the strength. The La oxide precipitates provide additional sites for dislocation nucleation simultaneously pinning the dislocation motion, thus obtaining higher strength and plasticity. Plastic deformation mechanism We have shown that incorporating the La oxide into the W matrix leads to the formation of nanoprecipitates at the grain boundaries, which induce an interface pinning effect during plastic deformation. Figure 3 a is an HRTEM image showing the interfacial district of the bcc → hcp transition with the orientation relationship (OR) following [111] bcc // [2 \(\:\stackrel{\text{-}}{\text{1}}\stackrel{\text{-}}{\text{1}}\) 0] hcp. As depicted in Fig. 3 a, we outline the grain boundary with white-colored dotted line, the La oxide nanoprecipitates with red-colored dotted circle, and the dual-phase structure with yellow-colored dotted circle which formed by the pinning effect. The bcc → hcp transition follows the classical Burgers mechanism 52 . During the phase transformation, there are six potential variants 53 , which are listed in Supplementary Table 1. Nevertheless, Burger-like transformations do not always produce all the predicted orientations. As the SAED pattern indicated in Fig. 3a1, the OR between the bcc and the hcp phases is [111] bcc // [2 \(\:\stackrel{\text{-}}{\text{1}}\stackrel{\text{-}}{\text{1}}\) 0] hcp, which is the same as the V1 phase transition in Supplementary Table 1. Figure 3 a demonstrates that the lattice distortion and phase transition occur under stress because of the pinning effect by the La oxide precipitates. Atomic-scale observations reveal that plastic deformation further activate composition-segregated bcc → hcp phase transition, where the dual-phase crystalline structure with bcc and hcp phase fraction continues to accommodate the plasticity induced by sliding. The phase transition structures can be manipulated to realize the synergetic enhancement of strength and ductility 54 , 55 . Specifically, Fig. 3 b depicts the Schematic diagrams of the Burgers orientation relationships and the lattice correspondence between bcc and hcp structures, the atomic-scale schematic diagrams dissect the atomic motion mechanism of composition segregation bcc → hcp phase transition procedure. The (110) plane of W matrix transforms to the (0001) plane of La oxide. The [111] direction of W matrix is parallel to the [2 \(\:\stackrel{\text{-}}{\text{1}}\stackrel{\text{-}}{\text{1}}\) 0] of La oxide 56 . Using two models of pure W and W-La crystal structure as depicted in Supplementary Fig. 4a, we further elucidated the strain distribution during deformation through MD simulations (Supplementary Fig. 4c). The strains in the pure W matrix are distributed at the grain boundaries, while in the W-La crystal structure, the strains exist uniformly in the dual-phase interface between W and La oxide phase during deformation. At elevated stress levels, numerous partial dislocations become active, contributing to the plasticity. Activated under high stress, abundant partial dislocations in the dual-phase play a critical role in the alloy’s deformation behavior, enhancing the strength. Additionally, Supplementary Fig. 4b demonstrates that the theoretical stress of the W-La cluster is higher than pure W, which further proves that the interface pinning effect and the dual-phase interface caused by the addition of La benefit the enhancement effect. The mechanical properties of La-doped and pure W wire Manufacturing W alloy wire with long length, high strength, outstanding plasticity, and superb hardness is a perennial objective. We contrasted the structural differences between the La-doped and pure W wire, here, we will assess the influence of the microstructure on the mechanical properties. Figure 4 a-b depicts the engineering and true stress-strain curves for two types of W wire. The La-doped W wires exhibit an ultimate engineering tensile strength of 6.92 GPa (true tensile strength of 7.21 GPa) with an elongation of 4.2%, which is the highest strength wire publicly reported at present, whereas the pure W wires have a tensile strength of 5.3 GPa (true tensile strength of 5.47 GPa) and an elongation of 3.15%. Both Fig. 4 a and Fig. 4 b indicate that the bcc → hcp phase transition induced by La oxides’ pinning effect in the cold-drawing could promote the strength-ductility synergy. Figure 4 c illustrates the strain hardening rates, derived from the engineering stress-strain curves, showing that the La-doped W wires are 2.35% and the pure W wires are 2.16%. The representative SEM image of La-doped W wire’s fracture morphology highlights a noticeable diameter shrinkage (Fig. 4 h). Marked with a yellow line, the fracture cross section’s diameter is 30.09 µm, resulting in a calculated shrinkage of 37.27%. A magnified view of the fracture surface morphology reveals a dense, fibrous distribution within the La-doped W wire, suggesting a multitude of fiber interfaces (Fig. 4 i). The interfacial interaction and plastic deformation, induced by the non-slip drawing process, create an in-situ protective layer, endowing the W wire with excellent tensile strength 57 . Measured by the nanoindentation technique, we compared the hardness of La-doped and pure W wires and verified the excellent beneficial effects of adding the La oxide on the tensile strength, plasticity, and hardness of W wire (Fig. 4 d-e). Figure 4 f shows the SEM image of the La-doped W wire’s cross-section, with the inset highlighting the nanoindentation impression. The strength and hardness of the La-doped W wire are significantly higher than that of pure W wire. As can be found in Fig. 4 g and Supplementary Table 2, the La-doped and pure W possess significantly higher ultimate tensile strength (UTS) compared with the reported saw wires, demonstrating an exceptional tensile capability. The materials used as saw wires include pure W 58 , 59 , 60 , 61 , K-doped W 62 , 63 , 64 , Re-doped W 65 , Ti 66 , 67 , 68 , and steel 69 , 70 . By using the same drawing method and equipment, we prepared the 25 µm diameter stainless steel (ss) wire, achieving a tensile strength of 3.00 GPa (Supplementary Fig. 5), which is much higher than many reported steel wires 69 , 70 . We demonstrate that the ice bath assisted non-slip drawing method provides an effective fabrication strategy for enhancing the strength of ultra-thin saw alloy wires. Moreover, the UTS of La-doped W wire is 30.6% higher than the pure W wire with the same manufacturing conditions, indicating the efficacy of La oxide precipitates’ pinning effect (as proved in Fig. 2 ) in improving the mechanical properties. The nano twins, SF, and severe lattice distortion vastly improve the elasticity and strength of the saw wires, which are also beneficial to the overall tensile-ductility bearing capability. In summary, coupling the ice bath assisted non-slip drawing with the La oxide addition; we prepared the ultra-thin La-doped W wires exhibiting s an exceptional strength-ductility synergy of tensile strength reaching 6.92 GPa, and fracture elongation of 4.2%, which are 30.6% and 33.3% higher than the pure W wire. Besides, we achieved a continuous drawing length of 50 km. Pinned at the grain boundaries, the hcp La oxide precipitates form a coherent interface with the bcc W matrix, inducing nano twins by lowering the SFE of W, triggering the lattice distortion and dislocations, confining the dislocation movement pathway, and altering the plastic deformation mechanism of W. The ice bath and non-slip drawing condition fabrication preserves the high-density defects and ultrafine grains, thus achieving a synergetic enhancement of strength-ductility. The nanodomain manipulation strategy opens the way of preparing high performance ultra-thin bcc metal wires with robust strength-ductility synergetic property. Methods Experimental details are available in the Supplementary Information. Declarations Data Availability All data generated or analyzed during this study are included in the published article and Supplementary Information and are available from the corresponding authors upon request. Acknowledgements This work was financially supported by the National Natural Science Foundation of China (Grant No. 52272079), the Military-Civilian Integration Fund of Shandong Province (No. JTJSXQ2021G3), the Natural Science Foundation of Shandong Province in China (No. ZR2020ME029), the Major Scientific and Technological Innovation Project of Shandong Province of China (2020CXGC010705, 2021ZLGX05, 2022ZLGX04). Author contributions T.Z. conceived the project. Y.Z. prepared the ultra-thin alloy wire, conducted mechanical test and carried out the TEM experiments. J.D. performed the DFT calculations. Y.L. performed the MD simulation. Y.Z. wrote the manuscript. All authors extensively discussed the data. T.Z., Y.L., J.Z. and F.X. revised the manuscript. Competing interests The authors declare no competing interests. Additional information Supplementary information The online version contains supplementary materials available at. 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On the process of transition of the cubic-body-centered modification into the hexagonal-close-packed modification of zirconium. Physica 1 , 561-586 (1934). Merkel S, Lincot A, Petitgirard S. Microstructural effects and mechanism of bcc-hcp-bcc transformations in polycrystalline iron. Physical Review B 102 , 104103 (2020). Sadeghilaridjani M, Pole M, Jha S, Muskeri S, Ghodki N, Mukherjee S. Deformation and tribological behavior of ductile refractory high-entropy alloys. Wear 478 , 12 (2021). Luo JS , et al. Laser surface treatment-introduced gradient nanostructured TiZrHfTaNb refractory high-entropy alloy with significantly enhanced wear resistance. J Mater Sci Technol 110 , 43-56 (2022). Yang WQ, Luo JS, Fu H, Cheung CF, Ruan HH, Yang XS. bcc → hcp phase transition significantly enhancing the wear resistance of metastable refractory high-entropy alloy. Scripta Materialia 221 , 6 (2022). Zhou TZ , et al. Ultra-compact MXene fibers by continuous and controllable synergy of interfacial interactions and thermal drawing-induced stresses. Nat Commun 13 , 13 (2022). Bochniak W, Piela K, Vinarski S, Lagoda M. Mechanical properties of tungsten wires after cycling deformation treatment. The International Journal of Advanced Manufacturing Technology 69 , 1955-1959 (2013). Zhao P , et al. Microstructure, mechanical behaviour and fracture of pure tungsten wire after different heat treatments. International Journal of Refractory Metals and Hard Materials 68 , 29-40 (2017). Kanazawa T, Iguchi Y, Kohyama N, Shimada A, Tsuji K, Nakai Y. Tungsten line having high tensile strength, and saw wire Patent WO2020137255 (2020). Watanabe S, Itoh Y. Wire including tungsten Patent WO2021153451 (2021). Riesch J , et al. Development of tungsten fibre-reinforced tungsten composites towards their use in DEMO—potassium doped tungsten wire. Physica Scripta 2016 , 014006 (2016). Terentyev D, Dubinko A, Riesch J, Lebediev S, Volkov I, Zhurkin E. Performance of tungsten fibers for Wf/W composites under cyclic tensile load. International Journal of Refractory Metals and Hard Materials 86 , 105094 (2020). Kanazawa T, Koyama N, Iguchi Y, Sasagawa Y, Shibata T, Tani T. Metal wire, saw wire, cutting apparatus, and method of manufacturing metal wire Patent US20190232404 (2019). Qiu N-n, Zhang Y, Zhang C, Tong H, Song X-p. Tensile properties of tungsten-rhenium wires with nanofibrous structure. International Journal of Minerals, Metallurgy, and Materials 25 , 1055-1059 (2018). Sakamoto J, Tada N, Uemori T. Tensile properties and slip deformation behavior of pure titanium thin wire with a small diameter-to-grain-size ratio. Materials Science and Engineering: A 863 , 144532 (2023). Semboshi S, Takasugi T. Fabrication of high-strength and high-conductivity Cu–Ti alloy wire by aging in a hydrogen atmosphere. Journal of alloys and compounds 580 , S397-S400 (2013). Kimura H, Takabayashi H. Steel used for high-strength high-fatigue-strength saw wires for cutting of single-crystal silicon ingot, contains specified amount of carbon, nitrogen, cobalt, molybdenum, chromium, aluminum, titanium, nitrogen, oxygen and iron Patent JP2014005493-A. He Z, Huang H, Yin F, Xu X. Development of a brazed diamond wire for slicing single-crystal SiC ingots. The International Journal of Advanced Manufacturing Technology 91 , 189-199 (2017). Chen CY, Sun M, Wang B, Zhou JA, Jiang ZH. Recent Advances on Drawing Technology of Ultra-Fine Steel Tire Cord and Steel Saw Wire. Metals 11 , 33 (2021). Additional Declarations There is NO Competing Interest. Supplementary Files SupplementaryInformation.docx SupplementaryMovie1.Onesingletungstenwirewith38.0XXmdiameterdrawing500gweight.mp4 Supplementary Movie 1. One single tungsten wire with 38.0μm diameter drawing 500g weight SupplementaryMovie2.DrawingfractureprocessofLadopedWwireinsituTEM.mp4 Supplementary Movie 2. Drawing fracture process of La-doped W wire in-situ TEM Cite Share Download PDF Status: Posted Version 1 posted You are reading this latest preprint version Research Square lets you share your work early, gain feedback from the community, and start making changes to your manuscript prior to peer review in a journal. As a division of Research Square Company, we’re committed to making research communication faster, fairer, and more useful. We do this by developing innovative software and high quality services for the global research community. Our growing team is made up of researchers and industry professionals working together to solve the most critical problems facing scientific publishing. Also discoverable on Platform About Our Team In Review Editorial Policies Advisory Board Help Center Resources Author Services Accessibility API Access RSS feed Manage Cookie Preferences © Research Square 2026 | ISSN 2693-5015 (online) Privacy Policy Terms of Service Do Not Sell My Personal Information {"props":{"pageProps":{"initialData":{"identity":"rs-4766443","acceptedTermsAndConditions":true,"allowDirectSubmit":true,"archivedVersions":[],"articleType":"Article","associatedPublications":[],"authors":[{"id":334191651,"identity":"4008cb34-b885-4838-ab1a-c8ea108eb781","order_by":0,"name":"Tao Zhang","email":"data:image/png;base64,iVBORw0KGgoAAAANSUhEUgAAAZAAAAAyAQMAAABI0h/eAAAABlBMVEX///8AAABVwtN+AAAACXBIWXMAAA7EAAAOxAGVKw4bAAAAyklEQVRIiWNgGAWjYLACxgYgwd7Y+OADMap54Fp4DjcbziBNi0R6mzQHMVrs2Q8ffPhzh12efOTDBmkGBjs53QZCtvCkJRtInkkuNryd2GBcwJBsbHaAoMNyzCQM25gTN85ObEiewXAgcRtBLfxvzCQS2+oTN8482HCYhygtEkBbDrYdTpwvwdjYTJyWG8+SDRvbjidu4ElsZpxhQIRf2PuTgSHWVp04v/348x8fKuzkCGqBAwOwSgNilYOAfAMpqkfBKBgFo2BEAQAJLES3s3WSOQAAAABJRU5ErkJggg==","orcid":"","institution":"Harbin Institute of Technology at Weihai","correspondingAuthor":true,"prefix":"","firstName":"Tao","middleName":"","lastName":"Zhang","suffix":""}],"badges":[],"createdAt":"2024-07-19 06:10:14","currentVersionCode":1,"declarations":"","doi":"10.21203/rs.3.rs-4766443/v1","doiUrl":"https://doi.org/10.21203/rs.3.rs-4766443/v1","draftVersion":[],"editorialEvents":[],"editorialNote":"","failedWorkflow":false,"files":[{"id":61809873,"identity":"e6093bd9-2d83-4b20-88d3-6489374c1212","added_by":"auto","created_at":"2024-08-05 20:17:17","extension":"png","order_by":1,"title":"Figure 1","display":"","copyAsset":false,"role":"figure","size":1814715,"visible":true,"origin":"","legend":"\u003cp\u003e\u003cstrong\u003eProperties and microstructure of La-doped and pure W wires.\u003c/strong\u003e \u003cstrong\u003ea\u003c/strong\u003e Fabrication method schematic for the La-doped W wire and enlarged views of traditional drawing wheel versus our improved version.\u003cstrong\u003e b \u003c/strong\u003eThe comparison of a reel with a length of 50 km La-doped W wire and an empty reel. \u003cstrong\u003ec \u003c/strong\u003eStatistical line chart of the La-doped W wire’s diameter fluctuation, distributing within 38.0±0.1% µm across a length of 50 km. \u003cstrong\u003ed \u003c/strong\u003eThe SEM image showing the diameters contrast of La-doped W wire and human hair. \u003cstrong\u003ee \u003c/strong\u003eA single 38.0 µm diameter La-doped W wire hanging a 500 g weight. \u003cstrong\u003ef \u003c/strong\u003eBright-field TEM image of the La-doped W wire. \u003cstrong\u003eg \u003c/strong\u003eEDS mapping of the precipitates within La-doped W wire. \u003cstrong\u003eh\u003c/strong\u003e The atomic content of precipitates, a W-La-O phase.\u003cstrong\u003e i \u003c/strong\u003eHRTEM image of nanoprecipitates at the grain boundaries. \u003cstrong\u003ej, k \u003c/strong\u003eThe statistic of La oxide precipitates and grain sizes in the La-doped W wire. \u003cstrong\u003el \u003c/strong\u003eSTEM image of the pure W wire. \u003cstrong\u003em\u003c/strong\u003e The grain size distribution statistic of pure W wire.\u003c/p\u003e","description":"","filename":"1.png","url":"https://assets-eu.researchsquare.com/files/rs-4766443/v1/523c6caa1b4735c457019110.png"},{"id":61811274,"identity":"8e06b70e-eb97-4fbb-9a3c-32bb767f62bf","added_by":"auto","created_at":"2024-08-05 20:25:17","extension":"png","order_by":2,"title":"Figure 2","display":"","copyAsset":false,"role":"figure","size":3799492,"visible":true,"origin":"","legend":"\u003cp\u003e\u003cstrong\u003eNano-twinned structures and the pinning effect of the precipitates.\u003c/strong\u003e \u003cstrong\u003ea\u003c/strong\u003e First-principle calculation results of the theoretical SFE of La-W alloy and pure W. \u003cstrong\u003eb\u003c/strong\u003e Bright-field TEM image of nano-twinned structures in the La-doped W wire. \u003cstrong\u003ec \u003c/strong\u003eEnlarged HRTEM image of one twin structure with an inset of HAADF-STEM image displaying an interlayer width of 1.415 nm. \u003cstrong\u003ed \u003c/strong\u003eHAADF-STEM image of a TB in a La oxide precipitate on the (211) plane, with an inset showing the corresponding FFT pattern taken along the [315//135] (ZA). \u003cstrong\u003ee, f \u003c/strong\u003eHRTEM images of typical dislocated SF region within La oxide precipitates.\u003cstrong\u003e g\u003c/strong\u003e HAADF-STEM image of the phase interface between the W-matrix and a La oxide precipitate\u003cstrong\u003e. h, i \u003c/strong\u003eHAADF-STEM images of La oxide precipitates highlighting dislocations produced in the precipitate region in the La-doped W wire, with FFT patterns along the (315) ZA. \u003cstrong\u003ej\u003c/strong\u003e The HRTEM image of a La oxide precipitate at a grain boundary with the corresponding GPA strain distribution on the ε\u003csub\u003exx\u003c/sub\u003e \u003cstrong\u003e(k) \u003c/strong\u003eand ε\u003csub\u003exy\u003c/sub\u003e\u003cstrong\u003e (l),\u003c/strong\u003e indicating lattice distortion due to precipitates induced from the drawing process.\u003c/p\u003e","description":"","filename":"2.png","url":"https://assets-eu.researchsquare.com/files/rs-4766443/v1/4c030a3eda9a7391af7a9afa.png"},{"id":61809875,"identity":"a924be69-0a04-470c-87f6-847f9d7f1d37","added_by":"auto","created_at":"2024-08-05 20:17:17","extension":"png","order_by":3,"title":"Figure 3","display":"","copyAsset":false,"role":"figure","size":216442,"visible":true,"origin":"","legend":"\u003cp\u003eSee image above for figure legend.\u003c/p\u003e","description":"","filename":"3.png","url":"https://assets-eu.researchsquare.com/files/rs-4766443/v1/be8a4e3538fee96d86ca2536.png"},{"id":61809878,"identity":"9178a478-1a7c-47af-bb9f-975f2d3c2b60","added_by":"auto","created_at":"2024-08-05 20:17:17","extension":"png","order_by":4,"title":"Figure 4","display":"","copyAsset":false,"role":"figure","size":1347325,"visible":true,"origin":"","legend":"\u003cp\u003e\u003cstrong\u003eMechanical properties of La-doped W wire versus pure W wire.\u003c/strong\u003e \u003cstrong\u003ea-e\u003c/strong\u003e Comparison of the engineering stress-strain curve, true stress-strain curve, work hardening rate, and nanoindentation curve for La-doped and pure W. \u003cstrong\u003ef\u003c/strong\u003e SEM image of the cross-section of La-doped W wire with an inset of the nanoindentation mark. \u003cstrong\u003eg\u003c/strong\u003e UTS versus wire diameter of the La-doped W wire and the pure W wire samples compared to the reported saw wires, such as W\u003csup\u003e58, 59, 60, 61\u003c/sup\u003e, K-doped W\u003csup\u003e62, 63, 64\u003c/sup\u003e, Re-doped W\u003csup\u003e65\u003c/sup\u003e, Ti\u003csup\u003e66, 67, 68\u003c/sup\u003e, and steel\u003csup\u003e69, 70\u003c/sup\u003e. \u003cstrong\u003eh\u003c/strong\u003e The SEM image of La-doped W wire fracture morphology and \u003cstrong\u003ei\u003c/strong\u003e the enlarged view in the white dotted line square area.\u003c/p\u003e","description":"","filename":"4.png","url":"https://assets-eu.researchsquare.com/files/rs-4766443/v1/8cd4e19302587b53b9864533.png"},{"id":64384415,"identity":"02c78514-b662-4490-a48d-5065c4cfdc80","added_by":"auto","created_at":"2024-09-12 12:19:34","extension":"pdf","order_by":0,"title":"","display":"","copyAsset":false,"role":"manuscript-pdf","size":9708006,"visible":true,"origin":"","legend":"","description":"","filename":"manuscript.pdf","url":"https://assets-eu.researchsquare.com/files/rs-4766443/v1/43a10e45-25b4-40ef-8828-29aa126705a7.pdf"},{"id":61809879,"identity":"0681ad92-ae66-4460-ab5b-acf8993bde50","added_by":"auto","created_at":"2024-08-05 20:17:17","extension":"docx","order_by":1,"title":"","display":"","copyAsset":false,"role":"supplement","size":4123369,"visible":true,"origin":"","legend":"\u003cp\u003e\u003cbr\u003e\u003c/p\u003e","description":"","filename":"SupplementaryInformation.docx","url":"https://assets-eu.researchsquare.com/files/rs-4766443/v1/f03ee533a4da236778282c49.docx"},{"id":61809876,"identity":"d83b1a58-0c94-4bb1-8cd2-62cfc063e840","added_by":"auto","created_at":"2024-08-05 20:17:17","extension":"mp4","order_by":2,"title":"","display":"","copyAsset":false,"role":"supplement","size":3861926,"visible":true,"origin":"","legend":"\u003cp\u003eSupplementary Movie 1. One single tungsten wire with 38.0μm diameter drawing 500g weight\u003c/p\u003e","description":"","filename":"SupplementaryMovie1.Onesingletungstenwirewith38.0XXmdiameterdrawing500gweight.mp4","url":"https://assets-eu.researchsquare.com/files/rs-4766443/v1/fd1229b34927ba3682cb1874.mp4"},{"id":61809877,"identity":"c0179ffb-9894-443a-934a-ed3e087f72fa","added_by":"auto","created_at":"2024-08-05 20:17:17","extension":"mp4","order_by":3,"title":"","display":"","copyAsset":false,"role":"supplement","size":7894622,"visible":true,"origin":"","legend":"\u003cp\u003eSupplementary Movie 2. Drawing fracture process of La-doped W wire in-situ TEM\u003c/p\u003e","description":"","filename":"SupplementaryMovie2.DrawingfractureprocessofLadopedWwireinsituTEM.mp4","url":"https://assets-eu.researchsquare.com/files/rs-4766443/v1/749db9870b449964abe793b5.mp4"}],"financialInterests":"There is \u003cb\u003eNO\u003c/b\u003e Competing Interest.","formattedTitle":"Synergetic strength-ductility enhancement of ultra-thin W wire by La oxide nanoprecipitates induced pinning effect","fulltext":[{"header":"Introduction","content":"\u003cp\u003eUltra-thin W wires are of great importance as saw wires in precision cutting of hard materials\u003csup\u003e\u003cspan citationid=\"CR1\" class=\"CitationRef\"\u003e1\u003c/span\u003e\u003c/sup\u003e. They also have extensive utilities in other purposes, such as plasma-facing materials\u003csup\u003e\u003cspan citationid=\"CR2\" class=\"CitationRef\"\u003e2\u003c/span\u003e, \u003cspan citationid=\"CR3\" class=\"CitationRef\"\u003e3\u003c/span\u003e, \u003cspan citationid=\"CR4\" class=\"CitationRef\"\u003e4\u003c/span\u003e\u003c/sup\u003e, medical radiation protection\u003csup\u003e\u003cspan citationid=\"CR5\" class=\"CitationRef\"\u003e5\u003c/span\u003e\u003c/sup\u003e, fine circuitry printing\u003csup\u003e\u003cspan citationid=\"CR6\" class=\"CitationRef\"\u003e6\u003c/span\u003e\u003c/sup\u003e, and cathode materials in magnetrons\u003csup\u003e\u003cspan citationid=\"CR7\" class=\"CitationRef\"\u003e7\u003c/span\u003e\u003c/sup\u003e. These applications leverage the unique properties of tungsten wires: ultra-thin diameter, high strength, excellent heat and corrosion resistance\u003csup\u003e\u003cspan citationid=\"CR8\" class=\"CitationRef\"\u003e8\u003c/span\u003e\u003c/sup\u003e. Utilized as the saw wires, if the ultra-thin W wires have a much higher tensile strength, the added benefits are much higher flexibility, a significantly larger cutting force, and considerably smaller instability of the cutting effect\u003csup\u003e\u003cspan citationid=\"CR9\" class=\"CitationRef\"\u003e9\u003c/span\u003e\u003c/sup\u003e. Typically, we use a series of cone pulleys mounted in a slip-drawing machine under heating and lubrication conditions to draw W wire. Under traditional conditions, the grain size tends to increase, nano twins (coupled with dislocations) are prone to annihilation, and the nanoprecipitates coarsen rapidly in medium and high temperatures due to the combined heat generated from external sources and dynamic friction, weakening the alloys\u003csup\u003e\u003cspan citationid=\"CR10\" class=\"CitationRef\"\u003e10\u003c/span\u003e\u003c/sup\u003e. As a result, the conventional heating assisted slip-drawing method fails to produce ultra-high strength W wires because of the thermal effects during fabrication, limiting the development of ultra-thin W wires.\u003c/p\u003e \u003cp\u003eTraditional methods, including twin crystals induction\u003csup\u003e\u003cspan citationid=\"CR11\" class=\"CitationRef\"\u003e11\u003c/span\u003e, \u003cspan citationid=\"CR12\" class=\"CitationRef\"\u003e12\u003c/span\u003e\u003c/sup\u003e, precipitate/solution strengthening\u003csup\u003e\u003cspan citationid=\"CR13\" class=\"CitationRef\"\u003e13\u003c/span\u003e, \u003cspan citationid=\"CR14\" class=\"CitationRef\"\u003e14\u003c/span\u003e\u003c/sup\u003e, and grain refinement\u003csup\u003e\u003cspan citationid=\"CR15\" class=\"CitationRef\"\u003e15\u003c/span\u003e, \u003cspan citationid=\"CR16\" class=\"CitationRef\"\u003e16\u003c/span\u003e\u003c/sup\u003e, are widely employed to augment and improve the alloy strength and toughness. Twin boundaries can improve the strength and plasticity of the alloy without compromising the fracture resistance by impeding and permitting incoming dislocations\u003csup\u003e\u003cspan citationid=\"CR17\" class=\"CitationRef\"\u003e17\u003c/span\u003e, \u003cspan citationid=\"CR18\" class=\"CitationRef\"\u003e18\u003c/span\u003e\u003c/sup\u003e. Lu et al. embedded the high-density thin twin boundaries in individual grains of copper, improving tensile strength by 10 times relative to the conventional coarse-grained polycrystalline counterpart\u003csup\u003e\u003cspan citationid=\"CR19\" class=\"CitationRef\"\u003e19\u003c/span\u003e\u003c/sup\u003e. High twin boundary (TB) densities in metals and alloys are achievable under certain conditions\u003csup\u003e\u003cspan citationid=\"CR20\" class=\"CitationRef\"\u003e20\u003c/span\u003e\u003c/sup\u003e, such as electrodeposition\u003csup\u003e\u003cspan citationid=\"CR21\" class=\"CitationRef\"\u003e21\u003c/span\u003e\u003c/sup\u003e, sputtering\u003csup\u003e\u003cspan citationid=\"CR22\" class=\"CitationRef\"\u003e22\u003c/span\u003e\u003c/sup\u003e, and severe plastic deformation\u003csup\u003e\u003cspan citationid=\"CR23\" class=\"CitationRef\"\u003e23\u003c/span\u003e, \u003cspan citationid=\"CR24\" class=\"CitationRef\"\u003e24\u003c/span\u003e\u003c/sup\u003e. While most of the manufacturing methods are accomplished in face-centered cubic (fcc) metals\u003csup\u003e\u003cspan citationid=\"CR25\" class=\"CitationRef\"\u003e25\u003c/span\u003e\u003c/sup\u003e, mainly in Cu\u003csup\u003e\u003cspan citationid=\"CR26\" class=\"CitationRef\"\u003e26\u003c/span\u003e\u003c/sup\u003e and steel\u003csup\u003e\u003cspan citationid=\"CR27\" class=\"CitationRef\"\u003e27\u003c/span\u003e\u003c/sup\u003e, few are in hcp metals like Ti\u003csup\u003e\u003cspan citationid=\"CR28\" class=\"CitationRef\"\u003e28\u003c/span\u003e\u003c/sup\u003e. Nevertheless, due to high stacking fault energy (SFE)\u003csup\u003e\u003cspan citationid=\"CR11\" class=\"CitationRef\"\u003e11\u003c/span\u003e, \u003cspan citationid=\"CR13\" class=\"CitationRef\"\u003e13\u003c/span\u003e, \u003cspan citationid=\"CR29\" class=\"CitationRef\"\u003e29\u003c/span\u003e, \u003cspan citationid=\"CR30\" class=\"CitationRef\"\u003e30\u003c/span\u003e\u003c/sup\u003e, bcc crystal structured metals exhibit low twinning dynamics\u003csup\u003e\u003cspan citationid=\"CR31\" class=\"CitationRef\"\u003e31\u003c/span\u003e\u003c/sup\u003e, deformation twins in most bcc metals are unstable and undergo spontaneous detwinning upon unloading\u003csup\u003e\u003cspan citationid=\"CR32\" class=\"CitationRef\"\u003e32\u003c/span\u003e\u003c/sup\u003e. Cost-effectively introducing stabilized nano-twinned structures into bcc metals has always been challenging. While solute atoms can engineer nano-twinned structures, segregation can supply a pinning effect for nano twin boundaries\u003csup\u003e\u003cspan citationid=\"CR33\" class=\"CitationRef\"\u003e33\u003c/span\u003e\u003c/sup\u003e, thereby it's feasible to induce nano twins by segregation in bcc metals. Chen and Yang et al. found that in bcc W electrode materials, La\u003csub\u003e2\u003c/sub\u003eO\u003csub\u003e3\u003c/sub\u003e particles, acting as a dispersion-strengthening phase, have a clear phase interface with the W matrix\u003csup\u003e\u003cspan citationid=\"CR34\" class=\"CitationRef\"\u003e34\u003c/span\u003e\u003c/sup\u003e, which was further identified as semi-coherent or incoherent interfacial relationship\u003csup\u003e\u003cspan citationid=\"CR35\" class=\"CitationRef\"\u003e35\u003c/span\u003e\u003c/sup\u003e, exerting a substantially positive effect on the mechanical properties.\u003c/p\u003e \u003cp\u003eHerein, we developed an ultra-thin La-doped W wire by introducing the La oxide particles into the W matrix, which forms the nanoprecipitates at the W grain boundaries. Transmission electron microscopy (TEM) results demonstrate that the hcp La oxide is uniformly pinned at the W grain boundaries, forming a coherent interface with the bcc W matrix. As molecular dynamics (MD) simulation reveals, plastic deformations occur at the region of La oxide during the deformation process, which significantly enhances the plastic deformation of grain boundaries and effectively elevates the uniform deformation, thereby promoting the strength and plasticity simultaneously. Moreover, the addition of La oxide induces the nano-twinned structures in W(La) solid solutions by reducing the SFE of W on the basis of the density-functional theory (DFT) calculations, thus hindering the dislocations movement, which further improves the tensile strength of W wires. In the manufacturing process, we used a non-slip drawing technique with an ice bath to enhance mechanical properties and circumvent the heat-induced coarsening of nanoprecipitates and twin annihilating. Cold drawing refines the grain size to below 23 nm, which is due to the formation of high-angle grain boundaries induced by intensive dislocations rearrangement\u003csup\u003e\u003cspan citationid=\"CR36\" class=\"CitationRef\"\u003e36\u003c/span\u003e, \u003cspan citationid=\"CR37\" class=\"CitationRef\"\u003e37\u003c/span\u003e, \u003cspan citationid=\"CR38\" class=\"CitationRef\"\u003e38\u003c/span\u003e\u003c/sup\u003e. The resulting ultra-thin W wire reached a peak tensile strength of 6.92 GPa, an elongation rate of 4.2%, and a continuous length surpassing 50 km. The synergy of nano twin boundaries, nanoprecipitates and ultrafine grains account for the La-doped W wire\u0026rsquo;s exceptionally high mechanical properties. The fabrication method can be applied to various ultra-thin metal wire manufacturing and shows great potential for industrial production.\u003c/p\u003e"},{"header":"Results and discussion","content":"\u003cdiv id=\"Sec3\" class=\"Section2\"\u003e \u003ch2\u003eThe microstructure analysis of the La-doped W wire\u003c/h2\u003e \u003cp\u003eFigure\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003ea illustrates the schematic of the non-slip drawing mechanism. With an initial diameter of 2.0 mm, we used the non-slip equipment to draw the raw La-doped W wire under ice bath conditions. As opposed to the traditional cone trolley slipping process, by employing a rubber-wrapped capstan to provide static friction, we maintained a constant grip on the wire (no slip friction), effectively cutting heat generation to a great extent. The concurrent use of an ice bath lowers the wire temperature, which helps preserve the fine grain size, twins, and high quantities of dislocations during the dynamic drawing process. The enhanced strength of W wires allows for further reduction of wire diameter. Figure\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003eb-e displays the drawing length, diameter distribution uniformity, wire diameter, and mechanical strength of the La-doped W wire. Figure\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003eb compares a reel winding 50 km of La-doped W wire with an empty reel. Figure\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003ec depicts the diameter tolerance of the La-doped W wire across a length of 50 km, demonstrating exceptional uniformity with a tolerance of approximately 38.0\u0026thinsp;\u0026plusmn;\u0026thinsp;0.1% \u0026micro;m. The high uniformity suggests that it is highly feasible to produce the La-doped W wire at long lengths with narrow diameter distribution, and the non-slip drawing method is also highly suitable for industrial applications. Figure\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003ed presents the scanning electron microscopy (SEM) image of an ultra-thin La-doped W wire alongside a human hair. With a remarkably smooth surface, the W wire\u0026rsquo;s diameter is 38.0 \u0026micro;m, approximately half the diameter of a human hair. Figure\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003ee testifies the strength of a single 38.0 \u0026micro;m diameter La-doped W wire, capable of lifting a 500 g weight (Supplementary Movie 1).\u003c/p\u003e \u003cp\u003eTo explore the effects of La element and the drawing process on microstructure, we performed the focused ion beam (FIB) etching on the cross sections of La-doped and pure W wires, both with a diameter of 38.0 \u0026micro;m (see inset in Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003ef). We employed the two TEM images from La-doped and pure W wires separately to compare the microstructures of post-etching specimens. Figure\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003ef reveals the lath-shaped grain morphology with a grain size of approximately 21.5 nm in the La-doped W sample. Figure\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003ei shows the high-resolution TEM (HRTEM) image of nanoprecipitates uniformly distributed at the grain boundaries, with a diameter of about 25.8 nm. Supplementary Fig.\u0026nbsp;1 shows an enlarged view of the precipitate in the grain boundary. We further analyzed the chemical composition of precipitates by the energy dispersive X-ray spectrometer (EDS) (Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003eg), revealing the W-La-O composition of the precipitate. The content of La in the precipitates is as high as 30.81% (Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003eh), indicating that La oxides mainly distribute at the grain boundaries in the precipitate form.\u003c/p\u003e \u003cp\u003eFigure\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003ej-k depicts the average dimensions of the La oxide precipitates and the grain sizes statistically. The precipitates and the grains sizes exhibit a narrow size distribution, with the nanoprecipitates between 0.4\u0026ndash;0.9 nm and grains between 11\u0026ndash;23 nm. The refined and axially oriented grains, coupled with enormous amounts of dislocations from the extreme plastic deformation under the cold drawing, contribute to enhanced tensile strength\u003csup\u003e\u003cspan citationid=\"CR39\" class=\"CitationRef\"\u003e39\u003c/span\u003e\u003c/sup\u003e. We prepared a pure W wire under identical conditions to clarify the effect of the La element on the microstructure and grain size. The aberration-corrected scanning TEM (STEM) image of pure W wires shows no precipitates at grain boundaries (Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003el). The statistical columnar graph exhibits that the average grain size of pure W wire ranges from 15 to 35 nm (Fig.\u0026nbsp;\u003cspan refid=\"Fig1\" class=\"InternalRef\"\u003e1\u003c/span\u003em), which is significantly larger than the La-doped W wire but still at the nanometer size level. The above results indicate that the non-slip ice bath drawing process restrains grain growth due to the smaller heat generation during the drawing process. The La-doped and pure W wires, processed using the same non-slip ice bath drawing technique, possess the nano-crystalline structures. The nano crystallines serve the purpose of accumulating geometrically necessary dislocations (GND), increasing the total dislocations, and inducing back stress\u003csup\u003e\u003cspan citationid=\"CR40\" class=\"CitationRef\"\u003e40\u003c/span\u003e\u003c/sup\u003e in the wire crystals, thus enhanced the tensile strength and augmented the elongation through strain hardening.\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003c/div\u003e\n\u003ch3\u003eNano twins and stacking fault structures in bcc metals\u003c/h3\u003e\n\u003cp\u003eThe SFE is an important intrinsic parameter of metal materials, which influences the deformation mechanism and mechanical properties of metal materials. The SFE is closely related to structural phase transformations, especially in severe plastic deformation. The change of SFE plays a decisive role in the metal deformation mechanism and grain refinement mechanism\u003csup\u003e\u003cspan citationid=\"CR41\" class=\"CitationRef\"\u003e41\u003c/span\u003e\u003c/sup\u003e. Typically, nano twins and stacking fault (SF) structures facilitate the plastic deformation in low SFE fcc metals, thus inducing high strength of metallic materials by obstructing mobile dislocations\u003csup\u003e\u003cspan citationid=\"CR19\" class=\"CitationRef\"\u003e19\u003c/span\u003e, \u003cspan citationid=\"CR42\" class=\"CitationRef\"\u003e42\u003c/span\u003e, \u003cspan citationid=\"CR43\" class=\"CitationRef\"\u003e43\u003c/span\u003e, \u003cspan citationid=\"CR44\" class=\"CitationRef\"\u003e44\u003c/span\u003e, \u003cspan citationid=\"CR45\" class=\"CitationRef\"\u003e45\u003c/span\u003e\u003c/sup\u003e, storing dislocations during plastic deformation\u003csup\u003e\u003cspan citationid=\"CR46\" class=\"CitationRef\"\u003e46\u003c/span\u003e\u003c/sup\u003e, and migrating under stress\u003csup\u003e\u003cspan citationid=\"CR47\" class=\"CitationRef\"\u003e47\u003c/span\u003e, \u003cspan citationid=\"CR48\" class=\"CitationRef\"\u003e48\u003c/span\u003e, \u003cspan citationid=\"CR49\" class=\"CitationRef\"\u003e49\u003c/span\u003e\u003c/sup\u003e. To further investigate the impact of La addition on the W crystal structure, we conducted first-principle calculations based on DFT models\u003csup\u003e\u003cspan citationid=\"CR50\" class=\"CitationRef\"\u003e50\u003c/span\u003e\u003c/sup\u003e to compare the SFE of bcc pure W and W-La alloys (Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003ea). We reveal that the SFE of the La-W alloys is 36.2% lower than that of pure W, demonstrating that adding La oxides reduces the SFE of bcc crystal structure W greatly, thereby making the binary La-W alloys more prone to induce twins and SF structure.\u003c/p\u003e \u003cp\u003eTo verify the results of the DFT calculation, we analyzed the FIB samples of La-doped W wire and the pure W wire by TEM. Figure\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003eb shows a bright-field TEM image of the La-doped W wire, revealing large quantities of nano-twinned structures exist within the bcc matrix. The TEM observation aligns with the simulation calculations on the SFE, as adding La reduces the SFE of W crystal structure in bcc metals, culminating in forming more nano-twinned structures under stress. Figure\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003ec presents an enlarged view of twins from Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003eb, and the inset in Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003ec displays the HRTEM image with an interlayer width of 1.41 nm. Figure\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003ed illustrates the high-angle annular dark-field scanning transmission electron microscopy (HAADF-STEM) image of a TB, highlighted by a yellow solid line, where the lattice spacings on either side of the line are both 0.13 nm, matching the (211) plane and correlate with the standard La\u003csub\u003e2\u003c/sub\u003eO\u003csub\u003e3\u003c/sub\u003e (JCPDS No: 05-0602), the inset image shows the corresponding selected fast Fourier transform (FFT), taken along [315//135] zone axis (ZA) at the yellow solid line area. The above observation confirms that the twinned structure originates in the La oxide precipitates area.\u003c/p\u003e \u003cp\u003eFigure\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003ee-f shows the HRTEM images of typical dislocated SF regions within the La oxide precipitates. The red dotted lines label the phase boundary between the matrix and the La oxide precipitate, and the yellow dotted lines denote the SF structures. Labeled by white lines, we measured one SF structure having a width of 2.08 nm and a length of 12.46 nm. The SFs present within the La oxide precipitate regions suggest that adding La facilitates the SF induction in precipitates. In contrast, despite having high intrinsic strength due to a nano-crystalline structure, the pure W wire exhibits no twinned structures in the TEM images, agreeing with the simulation predictions. Based on the above analysis, we confirm that adding La lowers the SFE and introduces twin and SF structures to bolster the strength of ultra-fine La-doped W wires.\u003c/p\u003e \u003cdiv id=\"Sec5\" class=\"Section2\"\u003e \u003ch2\u003ePinning effect in the La oxide precipitated region\u003c/h2\u003e \u003cp\u003eLabeled in a yellow solid line, Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003eg illustrates the HAADF-STEM image of the phase interface between the W-matrix and the La oxide precipitate. The lattice spacings on the W-matrix side are 0.08 nm and 0.11 nm, corresponding to the (400) and (220) planes, respectively, in agreement with standard W (JCPDS No: 04-0806). On the La oxide precipitate side, the lattice spacing is 0.13 nm, representing and matching the (211) plane of standard La\u003csub\u003e2\u003c/sub\u003eO\u003csub\u003e3\u003c/sub\u003e (JCPDS No: 05-0602). The inset shows an FFT pattern along the [315] ZA within the La oxide precipitate region. We prove that the ordered La oxide precipitates pinning the phase and twin boundaries. Figure\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003eh-i are the HAADF-STEM images of the La oxide precipitate outlined by the red-colored dotted circles, with widths of 0.94 nm and 1.77 nm, respectively. Both have FFT patterns along the [315] ZA from the circled areas. We also captured the partial dislocations existing in precipitates, marked with red \u0026lsquo;T\u0026rsquo; symbols, presenting that La oxide precipitates are prone to induce dislocations during the deformation process due to the pinning effect.\u003c/p\u003e \u003cp\u003eThe strain field surrounding the La oxide precipitate is mapped out using the geometrical phase analysis (GPA) approach. Figure\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003ej shows the HRTEM image of a La oxide precipitate at a grain boundary with GPA strain maps on the ε\u003csub\u003exx\u003c/sub\u003e (Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003ek) and ε\u003csub\u003exy\u003c/sub\u003e (Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003el), respectively. The GPA maps display the dislocations marked with yellow arrows at the La oxide precipitate, revealing the impact of the lattice distortion. The severe lattice distortion improves the stiffness and strength of the saw wires greatly, which are also beneficial to the overall tensile-bearing capability. The distortion indicates that a significant lattice strain exists near the La oxide precipitates, leading to elevated energy levels. La oxide doping stabilizes the grain boundaries by the pinning effect, thus stabilizing grain boundary segregation thermodynamically, reducing the grain boundary energy, and lessening the instability of nanocrystal metals\u003csup\u003e\u003cspan citationid=\"CR51\" class=\"CitationRef\"\u003e51\u003c/span\u003e\u003c/sup\u003e. The in-situ TEM movie of the La-doped W wire\u0026rsquo;s drawing fracture process (Supplementary Movie 2) and the fracture microstructure in STEM image (Supplementary Fig.\u0026nbsp;2) after drawing further confirm the La oxide precipitate\u0026rsquo;s pinning effect. The schematic illustration (Supplementary Fig.\u0026nbsp;3) shows the mechanisms of the pinning effect under stress. The pure W cracks along the nanograin under stress, while the La oxide in the grain boundary can absorb the stress energy and plays the role of pinning effect to prevent the fracture, thereby increasing the strength. The La oxide precipitates provide additional sites for dislocation nucleation simultaneously pinning the dislocation motion, thus obtaining higher strength and plasticity.\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003c/div\u003e\n\u003ch3\u003ePlastic deformation mechanism\u003c/h3\u003e\n\u003cp\u003eWe have shown that incorporating the La oxide into the W matrix leads to the formation of nanoprecipitates at the grain boundaries, which induce an interface pinning effect during plastic deformation. Figure\u0026nbsp;\u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003ea is an HRTEM image showing the interfacial district of the bcc \u0026rarr; hcp transition with the orientation relationship (OR) following [111] bcc // [2\u003cspan class=\"InlineEquation\"\u003e\u003cspan class=\"mathinline\"\u003e\\(\\:\\stackrel{\\text{-}}{\\text{1}}\\stackrel{\\text{-}}{\\text{1}}\\)\u003c/span\u003e\u003c/span\u003e0] hcp. As depicted in Fig.\u0026nbsp;\u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003ea, we outline the grain boundary with white-colored dotted line, the La oxide nanoprecipitates with red-colored dotted circle, and the dual-phase structure with yellow-colored dotted circle which formed by the pinning effect. The bcc \u0026rarr; hcp transition follows the classical Burgers mechanism\u003csup\u003e\u003cspan citationid=\"CR52\" class=\"CitationRef\"\u003e52\u003c/span\u003e\u003c/sup\u003e. During the phase transformation, there are six potential variants\u003csup\u003e\u003cspan citationid=\"CR53\" class=\"CitationRef\"\u003e53\u003c/span\u003e\u003c/sup\u003e, which are listed in Supplementary Table\u0026nbsp;1. Nevertheless, Burger-like transformations do not always produce all the predicted orientations. As the SAED pattern indicated in Fig.\u0026nbsp;3a1, the OR between the bcc and the hcp phases is [111] bcc // [2\u003cspan class=\"InlineEquation\"\u003e\u003cspan class=\"mathinline\"\u003e\\(\\:\\stackrel{\\text{-}}{\\text{1}}\\stackrel{\\text{-}}{\\text{1}}\\)\u003c/span\u003e\u003c/span\u003e0] hcp, which is the same as the V1 phase transition in Supplementary Table\u0026nbsp;1. Figure\u0026nbsp;\u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003ea demonstrates that the lattice distortion and phase transition occur under stress because of the pinning effect by the La oxide precipitates. Atomic-scale observations reveal that plastic deformation further activate composition-segregated bcc \u0026rarr; hcp phase transition, where the dual-phase crystalline structure with bcc and hcp phase fraction continues to accommodate the plasticity induced by sliding. The phase transition structures can be manipulated to realize the synergetic enhancement of strength and ductility\u003csup\u003e\u003cspan citationid=\"CR54\" class=\"CitationRef\"\u003e54\u003c/span\u003e, \u003cspan citationid=\"CR55\" class=\"CitationRef\"\u003e55\u003c/span\u003e\u003c/sup\u003e. Specifically, Fig.\u0026nbsp;\u003cspan refid=\"Fig3\" class=\"InternalRef\"\u003e3\u003c/span\u003eb depicts the Schematic diagrams of the Burgers orientation relationships and the lattice correspondence between bcc and hcp structures, the atomic-scale schematic diagrams dissect the atomic motion mechanism of composition segregation bcc \u0026rarr; hcp phase transition procedure. The (110) plane of W matrix transforms to the (0001) plane of La oxide. The [111] direction of W matrix is parallel to the [2\u003cspan class=\"InlineEquation\"\u003e\u003cspan class=\"mathinline\"\u003e\\(\\:\\stackrel{\\text{-}}{\\text{1}}\\stackrel{\\text{-}}{\\text{1}}\\)\u003c/span\u003e\u003c/span\u003e0] of La oxide\u003csup\u003e\u003cspan citationid=\"CR56\" class=\"CitationRef\"\u003e56\u003c/span\u003e\u003c/sup\u003e.\u003c/p\u003e \u003cp\u003eUsing two models of pure W and W-La crystal structure as depicted in Supplementary Fig.\u0026nbsp;4a, we further elucidated the strain distribution during deformation through MD simulations (Supplementary Fig.\u0026nbsp;4c). The strains in the pure W matrix are distributed at the grain boundaries, while in the W-La crystal structure, the strains exist uniformly in the dual-phase interface between W and La oxide phase during deformation. At elevated stress levels, numerous partial dislocations become active, contributing to the plasticity. Activated under high stress, abundant partial dislocations in the dual-phase play a critical role in the alloy\u0026rsquo;s deformation behavior, enhancing the strength. Additionally, Supplementary Fig.\u0026nbsp;4b demonstrates that the theoretical stress of the W-La cluster is higher than pure W, which further proves that the interface pinning effect and the dual-phase interface caused by the addition of La benefit the enhancement effect.\u003c/p\u003e \u003cp\u003e \u003c/p\u003e\n\u003ch3\u003eThe mechanical properties of La-doped and pure W wire\u003c/h3\u003e\n\u003cp\u003eManufacturing W alloy wire with long length, high strength, outstanding plasticity, and superb hardness is a perennial objective. We contrasted the structural differences between the La-doped and pure W wire, here, we will assess the influence of the microstructure on the mechanical properties. Figure\u0026nbsp;\u003cspan refid=\"Fig4\" class=\"InternalRef\"\u003e4\u003c/span\u003ea-b depicts the engineering and true stress-strain curves for two types of W wire. The La-doped W wires exhibit an ultimate engineering tensile strength of 6.92 GPa (true tensile strength of 7.21 GPa) with an elongation of 4.2%, which is the highest strength wire publicly reported at present, whereas the pure W wires have a tensile strength of 5.3 GPa (true tensile strength of 5.47 GPa) and an elongation of 3.15%. Both Fig.\u0026nbsp;\u003cspan refid=\"Fig4\" class=\"InternalRef\"\u003e4\u003c/span\u003ea and Fig.\u0026nbsp;\u003cspan refid=\"Fig4\" class=\"InternalRef\"\u003e4\u003c/span\u003eb indicate that the bcc \u0026rarr; hcp phase transition induced by La oxides\u0026rsquo; pinning effect in the cold-drawing could promote the strength-ductility synergy. Figure\u0026nbsp;\u003cspan refid=\"Fig4\" class=\"InternalRef\"\u003e4\u003c/span\u003ec illustrates the strain hardening rates, derived from the engineering stress-strain curves, showing that the La-doped W wires are 2.35% and the pure W wires are 2.16%. The representative SEM image of La-doped W wire\u0026rsquo;s fracture morphology highlights a noticeable diameter shrinkage (Fig.\u0026nbsp;\u003cspan refid=\"Fig4\" class=\"InternalRef\"\u003e4\u003c/span\u003eh). Marked with a yellow line, the fracture cross section\u0026rsquo;s diameter is 30.09 \u0026micro;m, resulting in a calculated shrinkage of 37.27%. A magnified view of the fracture surface morphology reveals a dense, fibrous distribution within the La-doped W wire, suggesting a multitude of fiber interfaces (Fig.\u0026nbsp;\u003cspan refid=\"Fig4\" class=\"InternalRef\"\u003e4\u003c/span\u003ei). The interfacial interaction and plastic deformation, induced by the non-slip drawing process, create an in-situ protective layer, endowing the W wire with excellent tensile strength\u003csup\u003e\u003cspan citationid=\"CR57\" class=\"CitationRef\"\u003e57\u003c/span\u003e\u003c/sup\u003e. Measured by the nanoindentation technique, we compared the hardness of La-doped and pure W wires and verified the excellent beneficial effects of adding the La oxide on the tensile strength, plasticity, and hardness of W wire (Fig.\u0026nbsp;\u003cspan refid=\"Fig4\" class=\"InternalRef\"\u003e4\u003c/span\u003ed-e). Figure\u0026nbsp;\u003cspan refid=\"Fig4\" class=\"InternalRef\"\u003e4\u003c/span\u003ef shows the SEM image of the La-doped W wire\u0026rsquo;s cross-section, with the inset highlighting the nanoindentation impression. The strength and hardness of the La-doped W wire are significantly higher than that of pure W wire.\u003c/p\u003e \u003cp\u003eAs can be found in Fig.\u0026nbsp;\u003cspan refid=\"Fig4\" class=\"InternalRef\"\u003e4\u003c/span\u003eg and Supplementary Table\u0026nbsp;2, the La-doped and pure W possess significantly higher ultimate tensile strength (UTS) compared with the reported saw wires, demonstrating an exceptional tensile capability. The materials used as saw wires include pure W\u003csup\u003e\u003cspan citationid=\"CR58\" class=\"CitationRef\"\u003e58\u003c/span\u003e, \u003cspan citationid=\"CR59\" class=\"CitationRef\"\u003e59\u003c/span\u003e, \u003cspan citationid=\"CR60\" class=\"CitationRef\"\u003e60\u003c/span\u003e, \u003cspan citationid=\"CR61\" class=\"CitationRef\"\u003e61\u003c/span\u003e\u003c/sup\u003e, K-doped W\u003csup\u003e\u003cspan citationid=\"CR62\" class=\"CitationRef\"\u003e62\u003c/span\u003e, \u003cspan citationid=\"CR63\" class=\"CitationRef\"\u003e63\u003c/span\u003e, \u003cspan citationid=\"CR64\" class=\"CitationRef\"\u003e64\u003c/span\u003e\u003c/sup\u003e, Re-doped W\u003csup\u003e\u003cspan citationid=\"CR65\" class=\"CitationRef\"\u003e65\u003c/span\u003e\u003c/sup\u003e, Ti\u003csup\u003e\u003cspan citationid=\"CR66\" class=\"CitationRef\"\u003e66\u003c/span\u003e, \u003cspan citationid=\"CR67\" class=\"CitationRef\"\u003e67\u003c/span\u003e, \u003cspan citationid=\"CR68\" class=\"CitationRef\"\u003e68\u003c/span\u003e\u003c/sup\u003e, and steel\u003csup\u003e\u003cspan citationid=\"CR69\" class=\"CitationRef\"\u003e69\u003c/span\u003e, \u003cspan citationid=\"CR70\" class=\"CitationRef\"\u003e70\u003c/span\u003e\u003c/sup\u003e. By using the same drawing method and equipment, we prepared the 25 \u0026micro;m diameter stainless steel (ss) wire, achieving a tensile strength of 3.00 GPa (Supplementary Fig.\u0026nbsp;5), which is much higher than many reported steel wires\u003csup\u003e\u003cspan citationid=\"CR69\" class=\"CitationRef\"\u003e69\u003c/span\u003e, \u003cspan citationid=\"CR70\" class=\"CitationRef\"\u003e70\u003c/span\u003e\u003c/sup\u003e. We demonstrate that the ice bath assisted non-slip drawing method provides an effective fabrication strategy for enhancing the strength of ultra-thin saw alloy wires. Moreover, the UTS of La-doped W wire is 30.6% higher than the pure W wire with the same manufacturing conditions, indicating the efficacy of La oxide precipitates\u0026rsquo; pinning effect (as proved in Fig.\u0026nbsp;\u003cspan refid=\"Fig2\" class=\"InternalRef\"\u003e2\u003c/span\u003e) in improving the mechanical properties. The nano twins, SF, and severe lattice distortion vastly improve the elasticity and strength of the saw wires, which are also beneficial to the overall tensile-ductility bearing capability.\u003c/p\u003e \u003cp\u003e \u003c/p\u003e \u003cp\u003eIn summary, coupling the ice bath assisted non-slip drawing with the La oxide addition; we prepared the ultra-thin La-doped W wires exhibiting s an exceptional strength-ductility synergy of tensile strength reaching 6.92 GPa, and fracture elongation of 4.2%, which are 30.6% and 33.3% higher than the pure W wire. Besides, we achieved a continuous drawing length of 50 km. Pinned at the grain boundaries, the hcp La oxide precipitates form a coherent interface with the bcc W matrix, inducing nano twins by lowering the SFE of W, triggering the lattice distortion and dislocations, confining the dislocation movement pathway, and altering the plastic deformation mechanism of W. The ice bath and non-slip drawing condition fabrication preserves the high-density defects and ultrafine grains, thus achieving a synergetic enhancement of strength-ductility. The nanodomain manipulation strategy opens the way of preparing high performance ultra-thin bcc metal wires with robust strength-ductility synergetic property.\u003c/p\u003e"},{"header":"Methods","content":"\u003cp\u003eExperimental details are available in the Supplementary Information.\u003c/p\u003e"},{"header":"Declarations","content":"\u003cp\u003e\u003cstrong\u003eData Availability\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eAll data generated or analyzed during this study are included in the published article and Supplementary Information and are available from the corresponding authors upon request.\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eAcknowledgements\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eThis work was financially supported by the National Natural Science Foundation of China (Grant No. 52272079), the Military-Civilian Integration Fund of Shandong Province (No. JTJSXQ2021G3), the Natural Science Foundation of Shandong Province in China (No. ZR2020ME029), the Major Scientific and Technological Innovation Project of Shandong Province of China (2020CXGC010705, 2021ZLGX05, 2022ZLGX04).\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eAuthor contributions\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eT.Z.\u0026nbsp;conceived the project. Y.Z. prepared the ultra-thin alloy wire, conducted mechanical test and carried out the TEM experiments. J.D. performed the DFT calculations. Y.L. performed the MD simulation. Y.Z. wrote the manuscript. All authors extensively discussed the data. T.Z., Y.L., J.Z. and F.X. revised the manuscript.\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eCompeting interests\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003eThe authors declare no competing interests.\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eAdditional information\u003c/strong\u003e\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eSupplementary information\u003c/strong\u003e The online version contains supplementary materials available at.\u003c/p\u003e\n\u003cp\u003e\u003cstrong\u003eCorrespondence\u003c/strong\u003e and requests for materials should be addressed to Junsong Zhang, Tao Zhang or Yujing Liu.\u003c/p\u003e"},{"header":"References","content":"\u003col\u003e\n\u003cli\u003eKamiya O\u003cem\u003e, et al.\u003c/em\u003e Development of fixed grain micro-saw wire and cutting performance. In: \u003cem\u003e7th Manufacturing-Engineering-Society International Conference (MESIC)\u003c/em\u003e). 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Recent Advances on Drawing Technology of Ultra-Fine Steel Tire Cord and Steel Saw Wire. \u003cem\u003eMetals\u003c/em\u003e \u003cstrong\u003e11\u003c/strong\u003e, 33 (2021).\u003c/li\u003e\n\u003c/ol\u003e"}],"fulltextSource":"","fullText":"","funders":[],"hasAdminPriorityOnWorkflow":false,"hasManuscriptDocX":true,"hasOptedInToPreprint":false,"hasPassedJournalQc":"","hasAnyPriority":true,"hideJournal":true,"highlight":"","institution":"","isAcceptedByJournal":false,"isAuthorSuppliedPdf":false,"isDeskRejected":"","isHiddenFromSearch":false,"isInQc":false,"isInWorkflow":false,"isPdf":false,"isPdfUpToDate":true,"isWithdrawnOrRetracted":false,"journal":{"display":true,"email":"[email protected]","identity":"researchsquare","isNatureJournal":false,"hasQc":true,"allowDirectSubmit":true,"externalIdentity":"","sideBox":"","snPcode":"","submissionUrl":"/submission","title":"Research Square","twitterHandle":"researchsquare","acdcEnabled":true,"dfaEnabled":false,"editorialSystem":"","reportingPortfolio":"","inReviewEnabled":false,"inReviewRevisionsEnabled":true},"keywords":"","lastPublishedDoi":"10.21203/rs.3.rs-4766443/v1","lastPublishedDoiUrl":"https://doi.org/10.21203/rs.3.rs-4766443/v1","license":{"name":"CC BY 4.0","url":"https://creativecommons.org/licenses/by/4.0/"},"manuscriptAbstract":"\u003cp\u003eUltra-thin W wire is one of the few tools that can cut precious hard materials, including wafers, silicon, and sapphire. Reducing the diameter of tungsten wire by increasing the strength of W wire is the only method to achieve lower material waste and higher precision. Here, we report an ultra-thin La-doped W wire produced by the ice bath assisted non-slip drawing, with a diameter of 38.0 μm and a continuous length exceeding 50 km, exhibiting a tensile strength up to 6.92 GPa with an elongation of 4.2%. Statistical analysis-assisted atomic resolution imaging and element distribution mapping and molecular dynamics (MD) simulations revealed that the hexagonal close-packed (hcp) La\u003csub\u003e \u003c/sub\u003eoxide precipitates pin at the grain boundaries and form a coherent interface with the body-centered cubic (bcc) W matrix, inducing the nano twins and local hcp region in bcc W matrix, which originates lattice distortion and dislocations, and altered the plastic deformation mechanism of W. The coherent W-La oxide interface enhances the plastic deformation of grain boundaries and effectively elevates the uniform deformation, thereby simultaneously enhancing the strength and ductility. The ice bath assisted non-slip drawing is applicable to diverse metal wires and is of high potential for scalable and industrial applications.\u003c/p\u003e","manuscriptTitle":"Synergetic strength-ductility enhancement of ultra-thin W wire by La oxide nanoprecipitates induced pinning effect","msid":"","msnumber":"","nonDraftVersions":[{"code":1,"date":"2024-08-05 20:17:12","doi":"10.21203/rs.3.rs-4766443/v1","editorialEvents":[{"type":"communityComments","content":0}],"status":"published","journal":{"display":true,"email":"[email protected]","identity":"researchsquare","isNatureJournal":false,"hasQc":true,"allowDirectSubmit":true,"externalIdentity":"","sideBox":"","snPcode":"","submissionUrl":"/submission","title":"Research Square","twitterHandle":"researchsquare","acdcEnabled":true,"dfaEnabled":false,"editorialSystem":"","reportingPortfolio":"","inReviewEnabled":false,"inReviewRevisionsEnabled":true}}],"origin":"","ownerIdentity":"4eb2a9c6-826c-4839-beaf-68695c8dc601","owner":[],"postedDate":"August 5th, 2024","published":true,"recentEditorialEvents":[],"rejectedJournal":[],"revision":"","amendment":"","status":"posted","subjectAreas":[{"id":35390184,"name":"Physical sciences/Materials science/Structural materials/Mechanical properties"},{"id":35390185,"name":"Physical sciences/Materials science/Structural materials/Metals and alloys"}],"tags":[],"updatedAt":"2024-11-07T22:00:08+00:00","versionOfRecord":[],"versionCreatedAt":"2024-08-05 20:17:12","video":"","vorDoi":"","vorDoiUrl":"","workflowStages":[]},"version":"v1","identity":"rs-4766443","journalConfig":"researchsquare"},"__N_SSP":true},"page":"/article/[identity]/[[...version]]","query":{"redirect":"/article/rs-4766443","identity":"rs-4766443","version":["v1"]},"buildId":"qtupq5eGEP_6zYnWcrvyt","isFallback":false,"isExperimentalCompile":false,"dynamicIds":[84888],"gssp":true,"scriptLoader":[]}