High-Pressure Synthesis of Copper-Based Rare-Earth Perovskite La1–xNdxCuO3 (0≤x≤1)
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摘要: 在高温高压条件下,利用自主设计加工的Walker型高压组件合成新型铜基稀土过渡金属钙钛矿La1–xNdxCuO3(0≤x≤1)。结构精修结果表明:La1–xNdxCuO3(0≤x≤0.4)具有菱方结构,空间群为
R¯3c ;当0.5≤x≤0.7时,该体系表现出R¯3c 菱方结构与Pnma正交结构共存的混合相;进一步增加Nd的掺杂比例,当0.8≤x≤1时样品具有单一的Pnma正交结构。获得了La1–xNdxCuO3(0≤x≤1)的完整结构相图,为深入研究稀土-3d过渡金属氧化物的磁性、金属-绝缘体相变等物性演化规律提供了新的材料选项。-
关键词:
- 高压合成 /
- 铜基稀土-3d过渡金属氧化物 /
- 金属绝缘体相变
Abstract: The copper-based rare-earth perovskites La1–xNdxCuO3(0≤x≤1) have been synthesized in the two-stage Walker-type high-pressure apparatus. The refined crystal structure results revealed that La1–xNdxCuO3 (0≤x≤0.4) adopts a rhombohedral structure with the space groupR¯3c . When 0.5≤x≤0.7, a mixed phase with bothR¯3c rhombohedral and Pnma orthorhombic structures was observed in the system. With a further increase in Nd3+ doping, the system exhibits a single Pnma orthorhombic phase when x=0.8, 0.9 and 1. A comprehensive structural phase diagram of La1–xNdxCuO3 (0≤x≤1) was established in this study, providing a new material platform for investigating the magnetic properties, metal-insulator transitions, and other physical property evolutions in rare-earth 3d transition metal oxides. -
具有钙钛矿结构的稀土-3d过渡金属氧化物RMO3(R为稀土,M为3d过渡金属)因表现出诸如多铁性[1–3]、高温超导[4]、巨磁阻效应[5]等奇异的物性而一直备受关注。从晶体结构来看,3d过渡金属阳离子M与氧离子形成共角连接的MO6八面体,稀土阳离子R位于MO6八面体的空隙中间。这种结构不仅可以容纳多种不同离子半径的稀土和过渡金属阳离子,造成MO6八面体的扭转和倾斜,而且还允许氧离子空位存在有序或无序排列。从电子结构来看,随着过渡金属阳离子3d价电子和稀土阳离子4f价电子的排布变化,考虑到电子间的强关联库仑相互作用,系统的轨道序和磁基态将发生显著改变。因此,稀土-3d过渡金属钙钛矿中存在结构、电荷、轨道和自旋多个量子自由度之间的相互耦合和竞争,为研究结构与物性的构效关系提供了绝佳平台。
在钙钛矿结构中,用几何结构容忍因子
t≡dR−O/(√2dM−O) 描述结构的晶格畸变,其中dR−O 和dM−O 分别表示稀土阳离子和过渡金属阳离子与配位氧离子之间的键长。实验发现,稀土-3d过渡金属氧化物RMO3的钙钛矿结构通常在1−δ⩽t⩽1 时保持稳定[6]。在高压作用下,体系将倾向于对称性更高的结构,从而减小晶格体积、增大物质密度。一方面,对于t<1−δ 的低对称非钙钛矿结构,其八面体在高压下扭转或畸变减弱,将导致晶格对称性提高,进而转变为钙钛矿结构;另一方面,对于t>1 的类钙钛矿共面变形体,由于在压力作用下R―O键比M―O键更易压缩,使得t 因子在高压下逐渐减小并趋近于1,最终成为钙钛矿结构。因此,高压可极大拓宽钙钛矿结构稳定存在的范围,在合成新型钙钛矿材料方面具有独特优势。然而,过去关于稀土-3d过渡金属钙钛矿RMO3的研究主要集中在过渡金属钒基[7–9]、铬基[10–12]、锰基[3, 13–14]、铁基[15–17]、钴基[18–20]和镍基[21–23]体系,对铜基稀土钙钛矿RCuO3的探索非常缺乏。其中一个主要原因是,含有反常高价态Cu3+的钙钛矿RCuO3需要在超高氧压下合成,使得该体系的样品制备异常困难。虽然LaCuO3可在5.0 GPa高压下合成[24]且已被广泛研究,但是随着稀土离子R半径的进一步减小,RCuO3钙钛矿结构的几何容忍因子t变得更小,因此需要更高压力条件才能合成。Zhou等[25]在1600 ℃、6.5 GPa的高温高压条件下合成了一系列La1–xNdxCuO3(0≤x≤0.6)固溶体,并系统研究了该体系的结构和物性演化规律,其中LaCuO3表现出金属性和增强的泡利顺磁性。Chen等[26]在15.0 GPa高压下合成出正交结构的钙钛矿NdCuO3样品,样品呈现绝缘体行为,但尚未系统研究其物性。以上结果表明,随着Nd3+的掺杂浓度提高,La1–xNdxCuO3(0.7≤x≤1)需要更高的合成压力,同时由于其σ*带逐渐变窄,将成为Cu3+单价钙钛矿体系中研究电子从巡游向局域渡越的关键材料。
为此,本研究将利用自主设计的高压组件,在Walker型二级推进压机上探索在最佳压力和温度条件下合成新型铜基稀土钙钛矿La1–xNdxCuO3(0≤x≤1)样品,并通过精修X射线衍射谱图获得详细的结构相图,为进一步研究压力对其晶格结构和电子结构的调控规律提供实验依据。
1. 实验技术
1.1 前驱体制备
将La2O3、Nd2O3 (Macklin公司,纯度99.9%)在900 ℃条件下预烧12 h,去除水分和附着气体;将预烧过的La2O3、Nd2O3和CuO粉末(Aladdin公司,纯度99.9%)按照La1–xNdxCuO3(0≤x≤1)的化学计量比混合均匀,研磨30 min以上;将混合粉末放入坩埚中,在马弗炉上于1000 ℃烧结20 h,获得La1–xNdxCuO3(0≤x≤0.4)样品的前驱体;将研磨均匀的原料放入球磨机,以55 Hz频率高速球磨12 h,获得La1–xNdxCuO3(0.5≤x≤1)样品的前驱体。高能球磨可以制造纳米级微观结构,使原料具有更小的粒径和更窄的粒度分布,促进其在非常规条件下发生反应[27–28],从而降低制备高浓度掺杂Nd3+样品的反应压力和温度条件。
1.2 高压高温制备
如图1所示,本研究通过在高温下分解KClO4产生氧气并封装在密闭金筒中提供高氧压环境[29],利用Walker型二级推进压机在高温高压条件下合成高质量的La1–xNdxCuO3(0≤x≤1)样品。
首先,自主设计加工了Walker型高压组件,通过建立组件尺寸、强度与压力的关系模型,优化其尺寸精度、材料强度和受力结构。通过在压机中对特定的压力标定材料加压,测量其电阻随外部油压的变化曲线[30–34],获得样品压强与外部油压的对应关系。每套组件由传压介质八面体(主要成分为氧化镁)、铬酸镧、氮化硼、铂筒、金箔、钼片和热电偶组成,其中热电偶放置在样品中心处,用来标定样品中心的反应温度。通过压力和温度校准,该高压组件可实现的最高压强和温度分别达到25 GPa和1300 ℃。
在此基础上,将样品的前驱体粉末冷压成圆柱体置于金箔筒中,并在样品两端装填近似等量的KClO4粉末,KClO4粉末与前驱体粉末的体积比约为1∶2,保证加热过程中释放过量的氧气与样品充分反应减少氧空位。合成La1–xNdxCuO3(0≤x≤1)样品所需的优化压力和温度条件见表1。实验结果表明,随着Nd3+离子掺杂浓度的提高,La1–xNdxCuO3(0.7≤x≤1)需要更高的合成压力。
表 1 La1–xNdxCuO3 (0≤x≤1)样品合成的压力和温度优化条件Table 1. Pressure and temperature conditions of synthesizing La1–xNdxCuO3 (0≤x≤1)Sample Pressure/GPa Temperature/℃ Time/min LaCuO3 6 1000 30 La0.9Nd0.1CuO3 6 1000 30 La0.8Nd0.2CuO3 6 1000 30 La0.7Nd0.3CuO3 10 1000 30 La0.6Nd0.4CuO3 10 1000 30 La0.5Nd0.5CuO3 10 1000 30 La0.4Nd0.6CuO3 10 1000 30 La0.3Nd0.7CuO3 14 1000 30 La0.2Nd0.8CuO3 14 1000 30 La0.1Nd0.9CuO3 14 1000 30 NdCuO3 14 1000 30 1.3 样品表征与精修
将合成的样品研磨30 min,用去离子水清洗3遍以上去除KCl杂质,利用Bruker D8 Advance X射线粉末衍射仪(PXRD,X射线波长λ=1.54056 Å)在衍射角度为20°~100°、步长为0.02°条件下测量PXRD数据,通过Fullprof 软件对La1–xNdxCuO3(0≤x≤1)的PXRD谱图进行Rietveld精修,获取晶体结构信息[35]。
2. 实验结果和讨论
图2显示了LaCuO3、La0.5Nd0.5CuO3、La0.2Nd0.8CuO3和NdCuO3的PXRD数据精修结果,其他更多组分的La1–xNdxCuO3(0≤x≤1)结构精修结果见表2,其中:RP、RWP、Chi2为精修品质因子。
表 2 La1–xNdxCuO3(0≤x≤1)的晶格参数Table 2. Structural parameters of La1–xNdxCuO3 (0≤x≤1)Sample Space group Lattice parameters/Å RP/% RWP/% Chi2 LaCuO3 R¯3c a=b=5.4976(6), c=13.2062(9) 3.05 5.59 7.01 La0.9Nd0.1CuO3 R¯3c a=b=5.4976(9), c=13.1917(5) 1.45 1.92 1.10 La0.8Nd0.2CuO3 R¯3c a=b=5.4988(9), c=13.1732(7) 1.25 1.68 0.79 La0.7Nd0.3CuO3 R¯3c a=b=5.4961(1), c=13.1625(7) 1.91 2.73 2.48 La0.6Nd0.4CuO3 R¯3c a=5.4933(9), c=13.1326(6) 2.41 4.14 7.09 La0.5Nd0.5CuO3 Phase 1: R¯3c (36.43%) a=b=5.4627(1), c=13.2988(9) 4.23 5.85 2.42 Phase 2: Pnma (63.57%) a=6.1821(1), b=7.3597(8), c=5.4318(7) 4.23 5.85 2.42 La0.4Nd0.6CuO3 Phase 1: R¯3c (43.49%) a=b=5.4571(7), c=13.2982(1) 1.25 1.68 0.79 Phase 2: Pnma (56.51%) a=6.5015(2), b=7.6552(6), c=5.3354(4) 1.25 1.68 0.79 La0.3Nd0.7CuO3 Phase 1: R¯3c (44.42%) a=b=5.4542(6), c=13.3191(9) 3.76 4.81 1.43 Phase 2: Pnma (55.58%) a=6.3189(6), b=7.2736(7), c=5.3706(8) 3.76 4.81 1.43 La0.2Nd0.8CuO3 Pnma a=6.3197(8), b=7.2408(1), c=5.3561(1) 7.75 9.92 2.20 La0.1Nd0.9CuO3 Pnma a=6.3045(3), b=7.2421(7), c=5.3462(9) 1.54 2.24 1.66 NdCuO3 Pnma a=6.3039(2), b=7.2176(2), c=5.3334(5) 1.72 2.48 1.42 LaCuO3具有空间群为
R¯3c 的菱方结构,而NdCuO3具有空间群为Pnma的正交结构,与之前报道[24, 26]一致。随着Nd3+掺杂浓度的增加,当x为0.5、0.6、0.7时,样品中存在R¯3c 菱方结构与Pnma正交结构共存的情况。这一结果与之前Zhou等[25]报道的La1–xNdxCuO3(0≤x≤0.6)保持菱方结构的结论不同,考虑可能与样品合成的压力和温度条件有关。进一步增大固溶体中Nd3+的掺杂浓度,发现样品在x≥0.8时完全转变为Pnma正交结构,并具有较大的晶胞参数和晶格畸变。基于以上结果,绘制了La1–xNdxCuO3(0≤x≤1)体系随Nd3+掺杂浓度变化的结构相图,如图3所示。该体系是Cu3+的单价钙钛矿,包含一个半填充的σ*窄带。LaCuO3在低温下表现出金属行为[36]。随着Nd3+掺杂增加,σ*的带宽将逐渐变窄,因此可在该材料中系统研究巡游σ*电子向局域e电子的渡越行为。与之类似的镍基RNiO3氧化物体系中,随着稀土离子半径的减小,在PrNiO3与NdNiO3之间发生了从金属到反铁磁绝缘体的一级相变,Ni―O键长和Ni―O―Ni键角的变化与巡游σ*电子向局域e电子的渡越密切相关[37]。之前的报道并未在La1–xNdxCuO3(0≤x≤0.6)样品中发现金属-绝缘体相变[25]。由于NdCuO3表现出绝缘体行为[26],后续可在具有更高Nd3+掺杂浓度的La1–xNdxCuO3 (0.7≤x≤1)样品中探索电子临界行为和磁性转变。
3. 结 论
通过自主设计加工的Walker型高压组件,实现了1300 ℃、25 GPa的高温高压合成条件。在此基础上,成功合成了La1–xNdxCuO3(0≤x≤1)系列样品,并对其进行了详细的结构研究。实验结果表明:当x在0~0.4范围内时,样品具有
R¯3c 菱方结构的单相;当x为0.5、0.6、0.7时,样品具有R¯3c 菱方结构与Pnma正交结构共存的混合相;而当x在0.8~1.0范围内时,样品具有Pnma正交结构的单相。该体系为深入研究Cu3+单价钙钛矿的结构和物性演化规律提供了材料基础。 -
表 1 La1–xNdxCuO3 (0≤x≤1)样品合成的压力和温度优化条件
Table 1. Pressure and temperature conditions of synthesizing La1–xNdxCuO3 (0≤x≤1)
Sample Pressure/GPa Temperature/℃ Time/min LaCuO3 6 1000 30 La0.9Nd0.1CuO3 6 1000 30 La0.8Nd0.2CuO3 6 1000 30 La0.7Nd0.3CuO3 10 1000 30 La0.6Nd0.4CuO3 10 1000 30 La0.5Nd0.5CuO3 10 1000 30 La0.4Nd0.6CuO3 10 1000 30 La0.3Nd0.7CuO3 14 1000 30 La0.2Nd0.8CuO3 14 1000 30 La0.1Nd0.9CuO3 14 1000 30 NdCuO3 14 1000 30 表 2 La1–xNdxCuO3(0≤x≤1)的晶格参数
Table 2. Structural parameters of La1–xNdxCuO3 (0≤x≤1)
Sample Space group Lattice parameters/Å RP/% RWP/% Chi2 LaCuO3 R¯3c a=b=5.4976(6), c=13.2062(9) 3.05 5.59 7.01 La0.9Nd0.1CuO3 R¯3c a=b=5.4976(9), c=13.1917(5) 1.45 1.92 1.10 La0.8Nd0.2CuO3 R¯3c a=b=5.4988(9), c=13.1732(7) 1.25 1.68 0.79 La0.7Nd0.3CuO3 R¯3c a=b=5.4961(1), c=13.1625(7) 1.91 2.73 2.48 La0.6Nd0.4CuO3 R¯3c a=5.4933(9), c=13.1326(6) 2.41 4.14 7.09 La0.5Nd0.5CuO3 Phase 1: R¯3c (36.43%) a=b=5.4627(1), c=13.2988(9) 4.23 5.85 2.42 Phase 2: Pnma (63.57%) a=6.1821(1), b=7.3597(8), c=5.4318(7) 4.23 5.85 2.42 La0.4Nd0.6CuO3 Phase 1: R¯3c (43.49%) a=b=5.4571(7), c=13.2982(1) 1.25 1.68 0.79 Phase 2: Pnma (56.51%) a=6.5015(2), b=7.6552(6), c=5.3354(4) 1.25 1.68 0.79 La0.3Nd0.7CuO3 Phase 1: R¯3c (44.42%) a=b=5.4542(6), c=13.3191(9) 3.76 4.81 1.43 Phase 2: Pnma (55.58%) a=6.3189(6), b=7.2736(7), c=5.3706(8) 3.76 4.81 1.43 La0.2Nd0.8CuO3 Pnma a=6.3197(8), b=7.2408(1), c=5.3561(1) 7.75 9.92 2.20 La0.1Nd0.9CuO3 Pnma a=6.3045(3), b=7.2421(7), c=5.3462(9) 1.54 2.24 1.66 NdCuO3 Pnma a=6.3039(2), b=7.2176(2), c=5.3334(5) 1.72 2.48 1.42 -
[1] FIEBIG M, LOTTERMOSER T, FRÖHLICH D, et al. Observation of coupled magnetic and electric domains [J]. Nature, 2002, 419(6909): 818–820. doi: 10.1038/nature01077 [2] WU J G, WANG J. Multiferroic behavior of BiFeO3–RTiO3 (Mg, Sr, Ca, Ba, and Pb) thin films [J]. Journal of Applied Physics, 2010, 108(2): 026101. doi: 10.1063/1.3452324 [3] DONG S, YU R, YUNOKI S, et al. Double-exchange model study of multiferroic RMnO3 perovskites [J]. The European Physical Journal B, 2009, 71(3): 339–344. doi: 10.1140/epjb/e2009-00225-1 [4] KHARE N. Handbook of high-temperature superconductor electronics [M]. New York: Marcel Dekker, 2003. [5] VON HELMOLT R, WECKER J, HOLZAPFEL B, et al. Giant negative magnetoresistance in perovskitelike La2/3Ba1/3MnO x ferromagnetic films [J]. Physical Review Letters, 1993, 71(14): 2331–2333. doi: 10.1103/PhysRevLett.71.2331 [6] GOODENOUGH J B, ZHOU J S. Orbital ordering in orthorhombic perovskites [J]. Journal of Materials Chemistry, 2007, 17(23): 2394–2405. doi: 10.1039/b701805c [7] MARTÍNEZ-LOPE M J, ALONSO J A, RETUERTO M, et al. Evolution of the crystal structure of RVO3 (R=La, Ce, Pr, Nd, Tb, Ho, Er, Tm, Yb, Lu, Y) perovskites from neutron powder diffraction data [J]. Inorganic Chemistry, 2008, 47(7): 2634–2640. doi: 10.1021/ic701969q [8] KUMARI S, PAUL S, RAJ S. Electronic structure of RVO3 (R=La and Y): effect of electron ( U) and exchange ( J) correlations [J]. Solid State Communications, 2017, 268: 20–25. doi: 10.1016/j.ssc.2017.09.017 [9] SAGE M H. Orbital, charge and magnetic order of RVO3 perovskites [D]. Groningen: University of Groningen, 2006. [10] SINGH K D, PANDIT R, KUMAR R. Effect of rare earth ions on structural and optical properties of specific perovskite orthochromates; RCrO3 (R=La, Nd, Eu, Gd, Dy, and Y) [J]. Solid State Sciences, 2018, 85: 70–75. doi: 10.1016/j.solidstatesciences.2018.10.001 [11] ZVEZDIN A K, GAREEVA Z V, CHEN X M. Multiferroic order parameters in rhombic antiferromagnets RCrO3 [J]. Journal of Physics: Condensed Matter, 2021, 33(38): 385801. doi: 10.1088/1361-648X/ac0dd6 [12] SIBANDA E T. Structural, magnetic and electronic properties of rare-earth based chromium oxides [D]. Johannesburg: University of Johannesburg, 2023. [13] ALONSO J A, MARTÍNEZ-LOPE M J, CASAIS M T, et al. Evolution of the Jahn-Teller distortion of MnO6 octahedra in RMnO3 perovskites (R=Pr, Nd, Dy, Tb, Ho, Er, Y): a neutron diffraction study [J]. Inorganic Chemistry, 2000, 39(5): 917–923. doi: 10.1021/ic990921e [14] KAJIMOTO R, MOCHIZUKI H, YOSHIZAWA H, et al. R-dependence of spin exchange interactions in RMnO3 (R=rare-earth ions) [J]. Journal of the Physical Society of Japan, 2005, 74(9): 2430–2433. doi: 10.1143/JPSJ.74.2430 [15] WARSHI M K, MISHRA V, SAGDEO A, et al. Structural, optical and electronic properties of RFeO3 [J]. Ceramics International, 2018, 44(7): 8344–8349. doi: 10.1016/j.ceramint.2018.02.023 [16] NAKHAEI M, KHOSHNOUD D S. Structural, magnetic, and electrical properties of RFeO3 (R=Dy, Ho, Yb & Lu) compounds [J]. Journal of Materials Science: Materials in Electronics, 2021, 32(11): 14286–14300. doi: 10.1007/s10854-021-05992-6 [17] SINGH N, RHEE J Y, AULUCK S. Electronic and magneto-optical properties of rare-earth orthoferrites RFeO3 (R= Y, Sm, Eu, Gd and Lu) [J]. Journal of the Korean Physical Society, 2008, 53(2): 806–811. doi: 10.3938/jkps.53.806 [18] ALONSO J A, MARTíNEZ-LOPE M J, DE LA CALLE C, et al. Preparation and structural study from neutron diffraction data of RCoO3 (R=Pr, Tb, Dy, Ho, Er, Tm, Yb, Lu) perovskites [J]. Journal of Materials Chemistry, 2006, 16(16): 1555–1560. doi: 10.1039/B515607F [19] ITOH M, HASHIMOTO J, YAMAGUCHI S, et al. Spin state and metal-insulator transition in LaCoO3 and RCoO3 (R=Nd, Sm and Eu) [J]. Physica B: Condensed Matter, 2000, 281/282: 510–511. doi: 10.1016/S0921-4526(99)01044-3 [20] WANG W R, XU D P, SU W H, et al. Raman active phonons in RCoO3 (R=La, Ce, Pr, Nd, Sm, Eu, Gd, and Dy) perovskites [J]. Chinese Physics Letters, 2005, 22(9): 2400. doi: 10.1088/0256-307X/22/9/072 [21] ZHOU J S, GOODENOUGH J B, DABROWSKI B. Exchange interaction in the insulating phase of RNiO3 [J]. Physical Review Letters, 2005, 95(12): 127204. doi: 10.1103/PhysRevLett.95.127204 [22] FERNÁNDEZ-DÍAZ M, ALONSO J A, MARTÍNEZ-LOPE M, et al. Charge disproportionation in RNiO3 perovskites [J]. Physica B: Condensed Matter, 2000, 276/278: 218–221. doi: 10.1016/S0921-4526(99)01416-7 [23] FREELAND J W, VAN VEENENDAAL M, CHAKHALIAN J. Evolution of electronic structure across the rare-earth RNiO3 series [J]. Journal of Electron Spectroscopy and Related Phenomena, 2016, 208: 56–62. doi: 10.1016/j.elspec.2015.07.006 [24] KARPPINEN M, YAMAUCHI H, ITO T, et al. High-pressure synthesis and thermal decomposition of LaCuO3 [J]. Materials Science and Engineering: B, 1996, 41(1): 59–62. doi: 10.1016/S0921-5107(96)01624-8 [25] ZHOU J S, ARCHIBALD W, GOODENOUGH J B. Approach to Curie-Weiss paramagnetism in the metallic perovskites La1– x Nd x CuO3 [J]. Physical Review B, 2000, 61(5): 3196–3199. doi: 10.1103/PhysRevB.61.3196 [26] CHEN B H, WALKER D, SUARD E, et al. High pressure synthesis of NdCuO3– δ perovskites (0≤ δ≤0.5) [J]. Inorganic Chemistry, 1995, 34(8): 2077–2083. doi: 10.1021/ic00112a020 [27] YU J B, LI Z H, SU W K. Synthesis of quinolines by N-Deformylation and aromatization via solvent-free, high-speed ball milling [J]. Synthetic Communications, 2013, 43(3): 361–374. doi: 10.1080/00397911.2011.599103 [28] XU W H, LI C Y. Efficient synthesis of cucurbiturils and their derivatives using mechanochemical high-speed ball milling (HSBM) [J]. High Performance Polymers, 2021, 33(5): 509–518. doi: 10.1177/0954008320967057 [29] HOSSEINI S G, POURMORTAZAVI S M, HAJIMIRSADEGHI S S. Thermal decomposition of pyrotechnic mixtures containing sucrose with either potassium chlorate or potassium perchlorate [J]. Combustion and Flame, 2005, 141(3): 322–326. doi: 10.1016/j.combustflame.2005.01.002 [30] HUSBAND R J, O’BANNON E F, LIERMANN H P, et al. Compression-rate dependence of pressure-induced phase transitions in Bi [J]. Scientific Reports, 2021, 11(1): 14859. doi: 10.1038/s41598-021-94260-y [31] SOYKAN C, ÖZDEMIR KART S. Structural, mechanical and electronic properties of ZnTe polymorphs under pressure [J]. Journal of Alloys and Compounds, 2012, 529: 148–157. doi: 10.1016/j.jallcom.2012.02.170 [32] CHEN X R, LI X F, CAI L C, et al. Pressure induced phase transition in ZnS [J]. Solid State Communications, 2006, 139(5): 246–249. doi: 10.1016/j.ssc.2006.05.043 [33] SUZUKI T, YAGI T, AKIMOTO S. Precise determination of transition pressure of GaAs [C]//22nd High Pressure Conference. 1981. [34] CHENG J G, ISHII T, KOJITANI H, et al. High-pressure synthesis of the BaIrO3 perovskite: a Pauli paramagnetic metal with a Fermi liquid ground state [J]. Physical Review B, 2013, 88(20): 205114. doi: 10.1103/PhysRevB.88.205114 [35] YOUNG R A. The Rietveld method [M]. Oxford: International Union of Crystallography, 1993. [36] BRINGLEY J F, SCOTT B A, LA PLACA S J, et al. Structure and properties of the LaCuO3– δ perovskites [J]. Physical Review B, 1993, 47(22): 15269. doi: 10.1103/PhysRevB.47.15269 [37] ZHOU J S, GOODENOUGH J B, DABROWSKI B. Transition from Curie-Weiss to enhanced Pauli paramagnetism in RNiO3 (R=La, Pr, … Gd) [J]. Physical Review B, 2003, 67(2): 020404. doi: 10.1103/PhysRevB.67.020404 -