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A medium-range structure motif linking amorphous and crystalline states

Nature Materials volume 20, pages 1347–1352 (2021)Cite this article

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An Author Correction to this article was published on 13 October 2021

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Abstract

Amorphous materials have no long-range order, but there are ordered structures at short range (2–5 Å), medium range (5–20 Å) and even longer length scales1,2,3,4,5. While regular6,7 and semiregular polyhedra8,9,10 are often found as short-range ordering in amorphous materials, the nature of medium-range order has remained elusive11,12,13,14. Consequently, it is difficult to determine whether there exists any structural link at medium range or longer length scales between the amorphous material and its crystalline counterparts. Moreover, an amorphous material often crystallizes into a phase of different composition15, with very different underlying structural building blocks, further compounding the issue. Here, we capture an intermediate crystalline cubic phase in a Pd-Ni-P amorphous alloy and reveal the structure of the medium-range order, a six-membered tricapped trigonal prism cluster (6M-TTP) with a length scale of 12.5 Å. We find that the 6M-TTP can pack periodically to several tens of nanometres to form the cube phase. Our experimental observations provide evidence of a structural link between the amorphous and crystalline phases in a Pd-Ni-P alloy at the medium-range length scale and suggest that it is the connectivity of the 6M-TTP clusters that distinguishes the crystalline and amorphous phases. These findings will shed light on the structure of amorphous materials at extended length scales beyond that of short-range order.

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Fig. 1: Precipitation of a cube phase.
Fig. 2: Observations of the cube phase using HRTEM.
Fig. 3: Illustration of the packing scheme for the cube phase and its backbone building block.
Fig. 4: Comparison between synchrotron X-ray results and calculated patterns of the 6M-TTP cluster, in reciprocal and real space.

Data availability

The data that support the findings of this study are available from the corresponding author upon request.

Code availability

The computational code used in this study is available upon request from the corresponding author.

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Acknowledgements

We wish to thank H. W. Kui for helpful discussions, Z. G. Ding for first-principles calculations and E. P. Gilbert for SANS measurements at QUOKKA in ANSTO, Australia. We also acknowledge the help of J. Zhang for ex-situ high-resolution synchrotron X-ray diffraction measurements in Taiwan Photon Source, J. Wu for preparing the ultrathin TEM samples by cryogenic focus ion beam in SUSTech Cryo-EM Facility Center and Z. Zhou of Tencent for developing the computer program for image matching. This work was supported by the National Natural Science Foundation of China (grant nos. 51871120, 51571170, 51520105001), the Natural Science Foundation of Jiangsu Province (grant no. BK20200019) and the Fundamental Research Funds for the Central Universities (grant nos. 30919011107, 30919011404). Z.W. and X.-L.W. acknowledge support by Guangdong-Hong Kong-Macao Joint Laboratory for Neutron Scattering Science and Technology (grant no. 2019B121205003). X.-L.W. was supported in part by grants from the Croucher Foundation (project no. CityU 9500034) and the Research Grants Council of Hong Kong SAR (grant no. JLFS/P-102/18). This research used the resources of the Advanced Photon Source, a US Department of Energy (DOE) Office of Science User Facility operated for the DOE Office of Science by Argonne National Laboratory under contract no. DE-AC02-06CH11357. We acknowledge the support of the Australian Centre for Neutron Scattering, Australian Nuclear Science and Technology Organization, in providing the neutron scattering research facilities used in this work.

Author information

Author notes

  1. These authors contributed equally: Si Lan, Li Zhu, Zhenduo Wu, Lin Gu.

Authors and Affiliations

  1. Herbert Gleiter Institute of Nanoscience, School of Materials Science and Engineering, Nanjing University of Science and Technology, Nanjing, China

    Si Lan, Huihui Kong, Jizi Liu, Sinan Liu, Gang Sha & Wei Liu

  2. Department of Physics, City University of Hong Kong, Kowloon, Hong Kong, China

    Si Lan, Qi Liu & Xun-Li Wang

  3. College of Materials Science and Technology, Nanjing University of Aeronautics and Astronautics, Nanjing, China

    Li Zhu & Yingang Wang

  4. Center for Neutron Scattering and Applied Physics, City University of Hong Kong Dongguan Research Institute, Dongguan, China

    Zhenduo Wu

  5. Beijing National Laboratory for Condensed Matter Physics and Collaborative Innovation Center of Quantum Matter, Institute of Physics, Chinese Academy of Sciences, Beijing, China

    Lin Gu & Qinghua Zhang

  6. Woodruff School of Mechanical Engineering, Georgia Institute of Technology, Atlanta, GA, USA

    Ruoyu Song

  7. SUSTech Cryo-EM Facility Center, Southern University of Science and Technology, Shenzhen, China

    Peiyi Wang

  8. Center for Advanced Structural Materials & Department of Materials Science and Engineering, City University of Hong Kong, Kowloon, Hong Kong, China

    Chain-Tsuan Liu

  9. X-ray Science Division, Argonne National Laboratory, Argonne, IL, USA

    Yang Ren

  10. Center for Neutron Scattering, City University of Hong Kong Shenzhen Research Institute, Shenzhen, China

    Xun-Li Wang

Authors
  1. Si Lan
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Contributions

S. Lan initiated the project and conceived the idea with L.Z., Z.W., Y.R. and X.-L.W. S. Lan, Y.R. and X.-L.W. supervised the project. S. Lan, Z.W., S. Liu and P.W. prepared the samples and TEM specimens. S. Lan and Y.R. performed in-situ synchrotron X-ray diffraction experiments at 11-ID-C of APS, ANL. S. Lan, L.Z., Z.W., Q.L., Y.R. and X.-L.W. analysed the PDF results. S. Lan, Z.W., J.L., P.W., Q.Z. and L.G. performed the TEM/STEM work. L.G. and Q.Z. performed HAADF–STEM, EDS mapping and did the related analysis, together with L.Z., Z.W., S. Liu and S. Lan. S. Lan and H.K. did the STM study. S. Lan and G.S. did the APT work. S. Lan and L.Z. constructed the structure model with the help of R.S. and Y.R. S. Lan and L.Z. drafted the manuscript together with Z.W., L.G., Y.W., C.-T.L., Y.R. and X.-L.W. All authors analysed and reviewed the results and provided input to this paper.

Corresponding authors

Correspondence to Si Lan, Yang Ren or Xun-Li Wang.

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Extended data

Extended Data Fig. 1 In-situ small-angle neutron scattering (SANS) study indicating the nano-precipitates prior to the final crystallization.

SANS profiles of the Pd41.25Ni41.25P17.5 MG at room temperature (RT) and 655.5 K, a temperature ~10 K lower than its final crystallization temperature. The inset is the pair distance distribution function (PDDF) of the Pd41.25Ni41.25P17.5 MG at 655.5 K.

Extended Data Fig. 2 More structural information about the cube phase obtained by STEM.

a-b, HAADF and Bright-field image for the Pd-Ni-P MG after precipitation. c-f, Fast-Fourier-Transform (FFT) patterns for the cube phase along [100], [110], [111] and [211] directions, respectively.

Extended Data Fig. 3 More evidence supporting the existence of the medium-range building block in the amorphous phase from the HAADF-STEM observation, and the Cs-corrected high-resolution transmission electron microscopy (HRTEM) images to observe the atomic structure of the cube phase.

a, Cs-corrected HAADF-STEM images for the cube phase taken with [211] zone axis. The upper right panel is the ACF processed two-dimensional images calculated from the red square regions in the cube phase. The bottom right panel is the ACF processed images from the yellow square regions in the amorphous matrix. b-e, Cs-corrected HRTEM images after the average background subtraction filtering (ABSF) for the cube phase taken with [100], [110], [111] and [211] zone axis, respectively.

Extended Data Fig. 4 Observing the cube phase and the amorphous Pd-Ni-P by scanning tunneling microscopy (STM).

a, STM image for Pd-Ni-P MG with the cube phase along with its higher magnification image in b. c, STM image for Pd-Ni-P alloy annealed at 583 K along with its higher magnification image in d. The 583-K sample retains fully amorphous structure.

Extended Data Fig. 5 Determining the composition distribution of the cube phase by EDS-mapping.

a and b, HAADF image of the cube phase taken with the [100] and [110] zone axis. c-e, Corresponding EDS maps for Pd, Ni, and P taken with the [110] zone axis, respectively. f, Line profiles of an atomic fraction of individual elements (Pd, Ni, and P) along the dotted yellow line in the EDS maps in Fig. 2e–g. g, Line profiles of an atomic fraction of individual elements (Pd, Ni, and P) along the dotted yellow line in the EDS maps in Extended Data Fig. 5c–e.

Extended Data Fig. 6 Determining the composition of the cube phase by atom probe tomography (APT).

a, Three-dimensional reconstructed P atom maps of the Pd-Ni-P MG with precipitates defined by iso-concentration surfaces at 5.1 nm−3 P (in green) using atom probe tomography. b, Two-dimensional elemental maps for the selected P-poor region (precipitate). c, One-dimensional concentration profiles through the center of the selected P-poor region (precipitate).

Extended Data Fig. 7 Schematic illustration of the packing scheme for the cube phase.

Two-dimensional view of the packing scheme along [100], [110] and [111] directions, respectively. Red balls are Pd and Ni atoms, whereas the blue balls represent P atoms. The orange-coloured polyhedron represents the Pd-enriched small cluster, and the blue-coloured polyhedron represents the Ni-enriched small cluster.

Extended Data Fig. 8 Evidence supporting the existence of the 6M-TTP clusters in the amorphous structure of Pd-Ni-P alloy by cluster-image comparisons and image simulation of an amorphous structure.

a, A comparison between the medium-range order in the 2D-DF HAADF-STEM image of the 583-K annealed Pd-Ni-P sample and the proposed 6M-TTP cluster. The yellow circles mark the position of the potential 6M-TTP clusters. The image is surrounded by seven enlarged 2D-DF HAADF-STEM images, in which the modelled 6M-TTP cluster and the corresponding STEM simulation results are superimposed. Three major symmetry directions, that is, [100], [110] and [111], can be clearly seen, which are similar to those of 6M-TTP projections. The comparisons are shown in sub-panels (I-II), (III-IV), and (V-VII), respectively. The bottom right panel is the FFT pattern demonstrating amorphous nature. b, A comparison between the medium-range order in the 2D-DF HAADF-STEM image of as-cast Pd-Ni-P sample and the proposed 6M-TTP cluster. The yellow circles mark the position of the 6M-TTP clusters. I-III, Enlarged 2D-DF HAADF-STEM images, in which the modelled 6M-TTP cluster and the corresponding STEM simulation results with [100], [110], and [111] orientations are superimposed, respectively. The bottom right panel is the FFT pattern demonstrating amorphous nature. c, Structure model of the random packed atomic structure with embedded 6M-TTP clusters and d, HREM simulation by multislice technology using xHREM software. Gray balls represent the metal atoms (Pd/Ni), and purple balls are the metalloid atoms (P). The circled regions are the embedded 6M-TTP clusters with [100], [110], and [111] orientations, respectively. e, The enlarged image of Extended Data Fig. 8a.

Extended Data Fig. 9 Illustrating the characteristic of the cube phase by selected area electron diffraction (SAED).

SAED patterns for: a as-cast, b cube phase precipitated and c leached Pd-Ni-P samples, respectively. d, Plots of diffraction intensity (I(Q)) versus scattering vector (Q) obtained by integrating the SAED pattern images. The arrows mark the reproduced shoulders in the Pd-Ni-P sample with the cube phase.

Extended Data Fig. 10 Schematic illustration of the chirality for the 6M-TTP.

Left panel: a polyhedral model for the 6M-TTP. The red and blue balls represent metal (Pd and Ni) and P atoms, respectively. Right panel: the corresponding configuration obtained by a mirror-symmetry operation.

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Lan, S., Zhu, L., Wu, Z. et al. A medium-range structure motif linking amorphous and crystalline states. Nat. Mater. 20, 1347–1352 (2021). https://doi.org/10.1038/s41563-021-01011-5

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