Atomic scale characterization of three-dimensional structure, magnetic properties and dynamic evolutions of materials by transmission electron microscopy

Zhong Xiao-Yan; Li Zhuo

doi:10.7498/aps.70.20202072

Abstract

Atomic scale characterization and manipulation is one of the physical bottlenecks, which needs to be broken when realizing atom manufacturing. The aberration-corrected transmission electron microscopy (TEM) is a powerful tool for structural characterization due to its exceptional spatial resolution. Therefore, it is very crucial to co-characterize atomic-scale three-dimensional structure and properties of atomic manufacturing materials by using TEM, which allows us to further understand the physics mechanism of atomic manipulation of materials. Nano-clusters and nanoparticles are two of the main objects in the studies of atomic manufacturing materials and devices, and possess rich physical and chemical properties and high manoeuverability. In this paper, we summarize the recent progress of quantitatively determining three-dimensional structures and magnetic properties of nanocluster, nanoparticles and nanograins, as well as their dynamic evolutions under the working conditions. The methodological breakthrough and development of electron microscopy techniques provide a solid foundation for precisely controlling atomic manufacturing materials.

Keywords:

Authors and contacts

1.
Department of Materials Science and Engineering, City University of Hong Kong, Kowloon 999077, China
2.
City University of Hong Kong Shenzhen Futian Research Institute, Shenzhen 518048, China
3.
Nanomanufacturing Laboratory (NML), City University of Hong Kong Shenzhen Research Institute, Shenzhen 518057, China
4.
State Key Laboratory of New Ceramics and Fine Processing, Key Laboratory of Advanced Materials (MOE), National Center for Electron Microscopy in Beijing, School of Materials Science and Engineering, Tsinghua University, Beijing 100084, China

Corresponding author: Zhong Xiao-Yan, xzhong25@cityu.edu.hk

Funds: Project supported by the National Natural Science Foundation of China (Grant Nos. 51822105, 52011530124, 11834009), the National Key R&D Program of China (Grant No. 2016YFB0700402), the Sino-German Mobility Programme at the Sino-German Center for Research Promotion (Grant No. M-0265), the Research Program of Shenzhen, China (Grant No. HZQB-KCZYB-2020031), the City University of Hong Kong, China (Grant Nos. 9610484, 9680291), the City University of Hong Kong Shenzhen Research Institute, the EU-HK Research and Innovation Cooperation Co-funding Mechanism (Grant No. E-CityU101/20), the Germany/Hong Kong Joint Research Scheme (Grant No. G-CityU102/20), and the European Union's Horizon 2020 Research and Innovation Programme (Grant Nos. 856538, “3D MAGiC”)

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Cited By

图 1 (a)加速电压为300 kV下的纳米金样品同轴全息图, 标尺为1 nm, 图中在3个孪晶的交接处用红色箭头标出了位错; 纳米金样品的三维(b)表面形貌和(c)原子构型, 并用不同的颜色标出不同晶体学取向的表面^[14]

Figure 1. (a) In-line holograms of a nanosized Au sample at the acceleration voltage of 300 kV. Scale bar is 1 nm. It is noteworthy that there are edge-on twin boundaries present in the imaged gold sample. At the intersection of three twin boundaries, a present end-on dislocation marked by the red arrow. (b) Surface morphology and (c) atomic structure views of the nanosized Au sample in three dimensions. The facets with different crystallographic orientations are highlighted with different colors^[14].

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图 2 原子级电子断层成像术示意图　(a)电子束聚焦在一个小点上并在样品上扫描以形成二维图像. 每个扫描位置的积分信号由环形暗场(ADF)探测器记录. (b)通过绕倾转轴旋转样品, 并在不同的倾转角度下测量一系列二维图像. (c)经过预处理和对中后, 通过分数傅里叶变换(FrFT)将系列倾转图像转换为傅里叶片层. 三维重构是通过傅里叶迭代算法来计算的. 通过三维重构, 可以跟踪和细化单个原子的坐标, 从而生成样品的三维原子模型^[49]

Figure 2. Schematic layout of atomic electron tomography (AET): (a) An electron beam is focused on a small spot and scanned over a sample to form a 2D image.The integrated signal at each scanning position is recorded by an annular dark-field (ADF) detector. (b) By rotating the sample around a tilt axis, a series of 2D images is measured at different tilt angles. (c) After preprocessing and alignment, the tilt series is inverted to Fourier slices by the fractional Fourier transform (FrFT). A 3D reconstruction is computed by using a Fourier-based iterative algorithm. From the 3D reconstruction, the coordinates of individual atoms are traced and refined to produce the 3D atomic model of the sample^[49].

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图 3 20 ℃和500 ℃下的Au₅₆₁团簇的高角环形暗场扫描透射显微(HAADF STEM)图像　(a)—(d) Au₅₆₁团簇HAADF STEM图像和(e)—(h)对应的不同带轴下立方八面体和Ino十面体的多片层法模拟像; (a), (b)在20 ℃下记录的实验像; (c), (d)在500 ℃下记录的实验像; (i)立方八面体和Ino十面体的几何构型及其旋转角度示意^[55]

Figure 3. High-angle annular dark-field scanning transmission electron microscopy (HAADF STEM) images of Au₅₆₁ clusters at 20 ℃ and 500 ℃: (a)–(d) HAADF STEM images of Au₅₆₁ clusters and (e)–(h) matching multi-slice electron scattering simulations of the cuboctahedron and Ino-decahedron at different orientations; (a), (b) experimental images recorded at 20 ℃; (c), (d) images recorded at 500 ℃; (i) rotation angle of the cuboctahedron and Ino-decahedron geometries^[55].

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图 4 Pt纳米颗粒在不同条件下的三维结构演变形貌　(a) 在真空中; (b), (d) 300 ℃下通入含5% H₂的Ar气; (c), (e) 300 ℃下通入O₂; 颗粒表面上不同晶面族的原子用不同颜色表示, 蓝色对应{100}, 粉色对应{110}, 紫色对应{111}, 灰色对应高指数面^[59]

Figure 4. Three dimensional morphology of structural evolution of Pt nanoparticles under different environmental conditions: (a) In vacuum; (b), (d) in 5% H₂ in Ar at 300 °C; (c), (e) in O₂ at 300 °C. The atoms are presented in different colors, according to the type of surface facet: blue = {100}, pink = {110}, purple = {111}, gray = higher index^[59].

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图 5 使用原子级电子断层成像术表征FePt颗粒中四维原子运动　(a)—(c) FePt纳米颗粒在累计退火时间为9、6和26分钟时的三维原子模型(Fe是红色、Pt是蓝色); (d)—(f) 在三种不同退火时间下富Pt的核心保持不变, 模型下方的浅灰色和深灰色投影分别显示了整个纳米颗粒及其核心; (g)—(i) 在3个退火时间沿 [010] 方向相同的纳米颗粒内部原子构型(Fe原子为红色, Pt原子为蓝色), 其中表面原子和亚表面的一小部分原子重新排列形成L1₀相(由椭圆形标出), 标尺为1 nm; (j)—(l) 颗粒形核点在退火时间为9、16和26分钟的分布, 其中点的颜色越淡代表其离表面越近, 颜色越暗表明其越靠近内部, $ \left\langle {100} \right\rangle $和$ \left\langle {111} \right\rangle $取向的刻面分别用绿色和品红色表示^[67]

Figure 5. Capturing four-dimensional atomic motion with atomic electron tomography. (a)–(c) Three-dimensional atomic models (Fe in red and Pt in blue) of an FePt nanoparticle with an accumulated annealing time of 9, 16 and 26 min, respectively. (d)–(f) The Pt-rich core of the nanoparticle (shown here) remained the same for the three annealing times. The light and dark grey projections below the models show the whole nanoparticle and the core, respectively. (g)–(i) The same internal atomic layer of the nanoparticle along the [010] direction at the three annealing times (Fe in red and Pt in blue), where a fraction of the surface and subsurface atoms had rearranged to form L1₀ phase (ellipses). Scale bar is 1 nm. (j)–(l) Distribution of the nucleation sites (dots) in particle with an accumulated annealing time of 9, 16 and 26 min, respectively, where the lighter colored dots are closer to the front side and the darker dots are closer to the back side of the nanoparticle. The $ \left\langle {100} \right\rangle $ and $ \left\langle {111} \right\rangle $ facets are in green and magenta, respectively^[67].

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图 6 纳米尺度协同测量单一NiFe₂O₄纳米晶粒的晶体结构、元素成分与定量磁矩　(a) 复合薄膜截面样品的透射电子显微(TEM)图像和选区衍射 (SAED) 花样, 在SrTiO₃基底上异质外延生长的钙钛矿BiFeO₃纳米晶粒和尖晶石NiFe₂O₄纳米晶粒的截面样品的低倍TEM图像, NiFe₂O₄纳米晶粒柱在[110]带轴下的单晶SAED花样; (b) 八面体Fe (Oct Fe)、八面体Ni (Oct Ni)、四面体Fe (Tet Fe)的占位分辨的磁圆二色谱; Oct Fe和Tet Fe之间的0.4 eV的化学位移差别反映了不同占位对称性上的差异, m_L/m_S为轨道自旋磁矩比, M_{Oct, Fe}, M_{Tet, Fe}和M_{Oct, Ni} 是Oct Fe, Tet Fe和Oct Ni的总磁矩, 单位为μ_B/atom^[73]

Figure 6. Nanoscale co-located measurement of crystallographic structure, elemental composition and quantitative magnetic moments of single NiFe₂O₄ nanograin: (a) Transmission electron microscopy (TEM) image and selected area electron diffraction (SAED) patterns of cross-sectional composite films. Low-magnification TEM image for cross-section sample of hetero-epitaxial composite thin films formed by perovskite BiFeO₃ and spinel NiFe₂O₄ nanograins on SrTiO₃ substrates. The single-crystalline SAED patterns are acquired from one NiFe₂O₄ nanograin along the [110] zone axis. (b) Site-specific magnetic circular dichroism spectra for Fe atoms at octahedral sites (Oct Fe), Ni atoms at octahedral sites (Oct Ni) and Fe atoms at tetrahedral sites (Tet Fe). A chemical shift of 0.4 eV between oct Fe peak and Tet Fe peak reveals the chemical shift for different site symmetries. m_L/m_S refers to the orbital to spin magnetic moment ratio. M_{Oct, Fe}, M_{Tet, Fe} and M_{Oct, Ni} are the total magnetic moments (the sum of spin and orbital magnetic moments) of Oct Fe, Tet Fe and Oct Ni in the units of μ_B/atom^[73].

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图 7 原子尺度协同测量Sr₂FeMoO₆的晶体结构、元素成分与定量磁矩(m_L/m_S为轨道自旋磁矩比)^[82,83]

Figure 7. Atomic scale co-located measurement of crystal structure, elemental composition and quantitative magnetic moment of Sr₂FeMoO₆. m_L/m_S refers to the orbital to spin magnetic moment ratio^[82,83].

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图 8 原位观测伪单畴的Fe₃O₄纳米颗粒的热磁行为　(a) 长对角轴的长度约为 150 nm的Fe₃O₄纳米颗粒的明场像以及对应的电子衍射花样; (b)—(h)依次在(b) 20 °C以及原位反应过程中加热到(c) 400 °C, (d) 500 °C和(e) 550 °C, 以及随后降温到 (f) 500 °C, (g) 400 °C和(h) 20 °C时记录的全息图重构出的磁感应强度分布图(标有FD字样的红色箭头代表诱导产生剩磁的外加饱和磁场的面内分量方向, 蓝色箭头表示为计算平均内势能而施加的额外的外磁场的方向); 所有磁感应强度分布图的等高磁轮廓线间距为 0.098 rad, 磁化方向使用箭头显示, 如色轮中所示; v代表漩涡的中心^[84]

Figure 8. Visualization of the thermomagnetic behavior of a small pseudo-single-domain Fe₃O₄ grain. (a) Bright-field transmission electron microscopy image of the individual Fe₃O₄ grain (about 150 nm in length across its long-diagonal axis), with associated electron diffraction pattern inset. (b)–(h) Magnetic induction maps reconstructed from holograms taken at (b) 20 °C (with the red arrow, labeled FD, showing the direction of the in-plane component of the applied saturating field to induce magnetic remanence, whereas the blue arrow shows the additional direction the field was applied for the calculation of the mean inner potential); during in situ heating to (c) 400 °C, (d) 500 °C, and (e) 550 °C; upon subsequent cooling to (f) 500 °C, (g) 400 °C, and (h) 20 °C. The contour spacing is 0.098 rad for all the magnetic induction maps, and the magnetization direction is shown using arrows, as depicted in the color wheel. v, center of the vortex^[84].

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图 9 原位观测氧化态对等轴Fe₃O₄纳米颗粒磁性的影响, 其中, (a)和(b)图分别是在原位加热至700 ℃ (a)之前和(b)之后的明场透射电子显微像, 原位加热过程是在9 mbar的O₂的环境下在环境透射电镜中加热8小时, 插图为对应纳米颗粒的选区电子衍射花样; 从原位加热(c)之前和(d)之后采集的全息图重构出的相位变化信息中获得的磁感应强度分布图, 展示出纳米颗粒的磁涡旋本征态, 等高磁轮廓线的间距是0.79 rad, 磁场方向用箭头表示, 与色轮对应; (e) Fe₃O₄ 颗粒在环境透射电镜中退火前(蓝色, γ-Fe₂O₃)和退火后(红色, Fe₃O₄)对应的电子能量损失谱中的Fe 2p的L_{2, 3}边, 黑色箭头表明了Fe₃O₄ 中的三种混合价态, 红色箭头强调了边前峰和边后峰的形成并表明样品在朝着γ-Fe₂O₃态氧化; (f)退火前(蓝色, γ-Fe₂O₃)和退火后(红色, Fe₃O₄) 颗粒中沿颗粒中心至边缘的剩余磁化强度分布, 黑色箭头表明了退火后整体剩磁的减少^[85]

Figure 9. Visualized effect of oxidation on the magnetization of an equiaxed Fe₃O₄ particle. Bright-field transmission electron microscopy images acquired (a) before and (b) after in situ heating to 700 ℃ under 9 mbar of O₂ for 8 h in an environmental transmission electron microscope (ETEM), with associated selected area electron diffraction patterns inset. (c), (d) Magnetic induction maps determined from the magnetic contribution to the phase shift, reconstructed from holograms taken (c) before and (d) after in situ heating, revealing the vortex nature of the particle. The contour spacing is 0.79 rad for both magnetic induction maps. The magnetization direction is shown using arrows, as depicted in the color wheel. (e) Associated electron energy-loss spectra of the Fe 2p L_{2, 3} edge acquired from the Fe₃O₄ particle before (blue) and after (red) annealing within the ETEM. Black arrows emphasize three differing intensities from the mixed-valence compound of Fe₃O₄, while the red arrows highlight formation of pre- and post-peaks that indicate oxidation towards γ-Fe₂O₃. (f) Line profiles across their centers of magnetic contribution of nanoparticles before (blue) and after (red) annealing. Black arrows in (f) illustrate the loss in overall magnetic remanence^[85].

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