材料研究学报, 2025, 39(5): 371-376 DOI: 10.11901/1005.3093.2024.328

研究论文

MOFs衍生C/LDH/rGO网状复合材料构筑高比容量水系锌离子电容器

刘艳云,1, 王娜1, 张志华2, 白文1, 刘云洁1, 陈勇强3, 李万喜1, 李瑀1

1.晋中学院材料科学与工程系 晋中 030619

2.太原海关技术中心 太原 030006

3.晋中学院化学与化工系 晋中 030619

MOFs Derived C/LDH/rGO Network Composite Materials for High Specific Capacity High-performance Aqueous Zinc Ion Capacitors

LIU Yanyun,1, WANG Na1, ZHANG Zhihua2, BAI Wen1, LIU Yunjie1, CHEN Yongqiang3, LI Wanxi1, LI Yu1

1.Department of Materials Science and Engineering, Jinzhong University, Jinzhong 030619, China

2.Customs Technology Center of Taiyuan, Taiyuan 030006, China

3.Department of Chemistry and Chemical Engineering, Jinzhong University, Jinzhong 030619, China

通讯作者: 刘艳云,副教授,312217642@qq.com,研究方向为储能材料与新型储能装置

责任编辑: 黄青

收稿日期: 2024-07-25   修回日期: 2024-12-13  

基金资助: 山西省基础研究自由探索项目(202103021224307)(202303021212509)(202203021222290)
山西省研究生教育创新计划(2021YJG336)
山西省科技创新青年人才团队

Corresponding authors: LIU Yanyun, Tel: 15698402116, E-mail:312217642@qq.com

Received: 2024-07-25   Revised: 2024-12-13  

Fund supported: Shanxi Province Basic Research Free Exploration Project(202103021224307)(202303021212509)(202203021222290)
Postgraduate Education Innovation Plan Project(2021YJG336)
Shanxi Province Science and Technology Innovation Youth Talent Team

作者简介 About authors

刘艳云,女,1984年生,博士

摘要

设计并合成了具有自支撑特性的MOFs衍生C/LDH/rGO网状复合材料,使用X射线衍射谱,扫描电子显微镜,X射线光电子能谱表征其结构和形貌。结果表明:这种MOFs衍生C/Ni-Co LDH为颗粒状结构,分散在rGO的片层中,形成了网状复合材料。用这种材料组装的锌离子电容器电流密度为1.0 A·g-1时比容量为248 F·g-1,循环1500次后电容保留率为97.1%。其原因是,这种复合材料中的MOFs衍生C/LDH/rGO网状结构,为电解液中的离子提供了大量的传输通道和赝电容活性位点。

关键词: 复合材料; 锌离子电容器; 水热法; 能量密度

Abstract

Aqueous Zn ion hybrid capacitors (ZICs), as an emerging energy storage device with low cost, high operational safety and low redox potential, have become a research hotspot in the field of energy storage. This paper focuses on the important research of low energy density of capacitor electrode materials in ZICs. Metal-organic frameworks (MOFs)-derived carbon (C)/layered double hydroxides (LDH)/graphene (rGO) network composite materials with self-supporting characteristics are designed and synthesized. The structure and morphology of the material were characterized by X-ray diffractometer, scanning electron microscope and X-ray photoelectron spectroscopy. The results showed that the MOFs-derived C/ Ni-Co LDH particles were granular structure, dispersed on lamellae of the rGO, forming a network composite material. The specific capacitance of the Zn ion capacitor assembled by this material can reach 248 F·g-1 at a current density of 1.0 A·g-1, which is much larger than the specific capacitance of rGO (142 F·g-1). After 1500 cycles, the capacitance retention rate of the Zn ion capacitor is still as high as 97.1%. The network structure not only provides more transmission channels for electrolyte ions, but also provides more pseudocapacitive active sites. The completion of this paper provides some theoretical guidance and practical significance for the development of high specific energy storage devices.

Keywords: composite materials; zinc ion capacitors; hydrothermal method; energy density

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本文引用格式

刘艳云, 王娜, 张志华, 白文, 刘云洁, 陈勇强, 李万喜, 李瑀. MOFs衍生C/LDH/rGO网状复合材料构筑高比容量水系锌离子电容器[J]. 材料研究学报, 2025, 39(5): 371-376 DOI:10.11901/1005.3093.2024.328

LIU Yanyun, WANG Na, ZHANG Zhihua, BAI Wen, LIU Yunjie, CHEN Yongqiang, LI Wanxi, LI Yu. MOFs Derived C/LDH/rGO Network Composite Materials for High Specific Capacity High-performance Aqueous Zinc Ion Capacitors[J]. Earth Science, 2025, 39(5): 371-376 DOI:10.11901/1005.3093.2024.328

为了弥补化石燃料的消耗和保护环境,发展新型高效储能装置至关重要[1~6]。离子混合电容器是电池和超级电容器的结合,是一种很有前途的电化学储能装置[7]。非水系锂离子电容器(LICs)的能量密度高和使用寿命长,引起了广泛的关注[8]。但是,这种电容器的成本较高和所用的锂资源稀缺。水系锌离子混合电容器(ZICs)的成本低廉、操作安全和氧化还原电位较低,是目前的研究热点[9~11]

ZICs是一种不对称电容器,使用电池电极材料可提高其能量密度。但是与锌离子电池(ZIBs)相比,ZICs的能量密度还可进一步提高。根据“短板效应”,电容电极材料的容量是影响其能量密度的关键因素。目前常见的电容电极是炭材料[12~15],研发具有高比容量的电容电极材料,对于开发高比能量的ZICs有重要的意义。金属有机骨架(MOFs)材料是一种超高孔隙率和巨大比表面积的多孔材料,有丰富的微/介孔结构。微/介孔结构的比表面积较大,其孔尺寸可调和有金属活性中心,是超级电容器极有前景的电极材料[16]。MOFs衍生层状双金属氢氧化物(LDH)具有复杂的组分和多种金属间的协同作用,其电化学活性远高于单一金属氢氧化物[17]。目前限制LDH用于电容电极材料的主要影响因素,是其较低的电导率和活性物质易团聚。碳材料如石墨烯(rGO)、碳纳米管等,其电导率较高和成本较低,将其与LDH复合可制备高性能复合电极材料[18,19]。有人用液相法合成的Ni-Al LDH/rGO复合材料,其比电容(629.8 F·g-1 at 1 A·g-1)比LDH 材料(517.8 F·g-1 at 1 A·g-1)的高[8]。但是,MOFs衍生复合材料用于ZICs使用锌离子水溶液为电解液时二价锌离子在水合离子尺寸、电荷携带量、扩散动力学等方面与H+、Na+、K+等一价离子有很大的差异。同时,对水系ZICs储能机制还有待深入认识。MOFs衍生复合电极材料中的导电炭黑和粘结剂使其在充放电过程中电极物相易受干扰。本文合成具有自支撑特性的MOFs衍生C/Ni-Co LDH/rGO网状复合材料,用这种材料作电容电极组装水系锌离子电池(ZICs)并研究其性能。

1 实验方法

1.1 实验用试剂和设备仪器

实验用试剂:六水合硝酸钴、2-甲基咪唑、甲醇、无水乙醇和硝酸镍(均为分析纯)。

实验用设备仪器:电子天平(FA2004),电热鼓风干燥箱(DGG-9030BD),高速离心机(HC-3018),管式炉(SK-1200),冷冻干燥机(FD-1A-50),电化学工作站 (CHI660E)。

1.2 MOFs衍生C/LDH/rGO网状复合材料和rGO电极材料的制备

将2 mmol CO(NO3)2·6H2O(1.164 g)溶到50 mL甲醇溶液中,然后加入溶有8 mmol 2-甲基咪唑(1.314 g)的50 mL甲醇溶液,用磁力搅拌器搅拌0.5 h后静置24 h。反应结束后收集沉淀并用无水乙醇离心洗涤,然后将产物在60 ℃恒温干燥箱中干燥12 h制备出ZIF-67单体。将ZIF-67单体放入400 ℃管式炉中在N2气氛中碳化2 h,得到MOFs衍生C/ZIF-67。升温速率为2 ℃·min-1

将制得的MOFs衍生C/ZIF-67样品溶解在50 mL乙醇溶液中,超声1 h后再溶解180 mg的Ni(NO3)2·6H2O,磁力搅拌0.5 h。然后进行回流操作,将温度升高到90 ℃反应1 h。反应完成后用无水乙醇充分洗涤沉淀,然后将其放入60 ℃烘箱中干燥12 h,得到MOFs衍生C/Ni-Co LDH。

将用Hummers法制备的氧化石墨粉末[20]分散在水中,超声波处理2 h后得到氧化石墨烯悬浮液(GO,2 mg/mL)。将MOFs衍生C/Ni Co LDH粒子与GO水溶液在170 ℃水热反应5 h,反应完成后取出产物并将其在真空冻干机里冻干48 h,得到MOFs衍生C/LDH/rGO网状复合材料。

将50 mL的GO水溶液在170 ℃水热反应5 h,反应完成后取出产物并将其在真空冻干机里冻干48 h,得到rGO电极材料。

1.3MOFs衍生C/LDH/rGO网状复合材料为正极的锌离子电容器的组装和性能测试

以MOFs衍生C/LDH/rGO网状复合材料为正极材料、锌箔为负极、0.5 mol/L硫酸锌为电解液,组装锌离子电容器。为了比较,以rGO为正极材料制备锌离子电容器。根据恒流充放电曲线(CP)比电容(F·g-1)为

C=2IVdtmΔV

式中C是比容量,I是电流,V是电位窗口,t是放电时间,m是正极的质量。

2 结果和讨论

图1为MOFs衍生C/LDH/rGO网状复合材料的制备流程,图2a为其XRD谱。谱中38.3°、44.8°、65.3°、78.1°、88°处的衍射峰分别对应PDF#73-1702卡片(222) (400) (440) (622) (444)晶面,其它成分,如石墨烯、MOFs衍生碳为无定型的,在XRD谱中没有衍射峰[21]图2b~d给出了MOFs衍生复合材料不同放大倍数的SEM照片,可见这种复合材料呈现网络状结构。这可能是氧化石墨烯的水热过程中自组装成了片层结构,在片层表面包裹一些颗粒状MOFs衍生C/Ni-Co LDH粒子。图2e~h给出了MOFs衍生复合材料的能谱。可以看出,这种复合材料含有元素C、N、O、Co等元素,均匀地分散在复合材料中,元素Ni的含量较低观测不到。

图1

图1   MOFs衍生C/LDH/rGO网状复合材料的制备流程

Fig.1   Preparation flow chart of MOFs derived C/LDH/rGO network composite materials


图2

图2   MOFs衍生C/LDH/rGO网状复合材料的XRD谱、SEM图和能谱图

Fig.2   XRD (a), SEM (b~d) and EDS mapping images (e~h) of MOFs derived C/LDH/rGO network composite materials


可用XPS检测复合材料中的元素和元素的化学环境。图3a为MOFs衍生复合材料的XPS全谱,谱中的附表为复合材料中元素的原子分数,还可见复合材料中主要有Co、O、C、N、Ni五种元素。图3b给出了C 1s的XPS谱,谱中有四种不同类型分别位于282.8、283.15、284.5和287.4 eV的碳峰:C―C、C=C、C―O和C=O[22]图3c给出了Co 2p的XPS谱,780.4 eV和784.2 eV是热解反应后氧化过程中产生的Co2+和Co3+的峰,表明在复合材料中有Co3+与Co2+ [23];在O 1s的XPS谱(图3d)中282.9 eV、283.16 eV处出现两个峰,分别对应M―O―M的晶格氧和M―O―H的羟基氧。

图3

图3   MOFs衍生C/LDH/rGO网状复合材料的XPS谱图

Fig.3   XPS spectra of MOFs derived C/LDH/rGO network composite materials

(a) full spectrum, (b) C 1s spectrum, (c) Co 2p spectrum, (d) O 1s spectrum


图4a为用MOFs衍生C/LDH/rGO网状复合材料组装的锌离子电容器的反应过程模拟,图4b给出了这种锌离子电容器在不同扫描速度下的CV图。可以看出,四条曲线均出现氧化还原峰,表明电极材料发生了赝电容反应。从图4a可见,电压提高时溶液中的阴离子SO42-流向正极,嵌入电极材料而Zn2+脱出;电压降低时溶液中的Zn2+流向正极,嵌入电极材料而SO42-脱出。随着扫描速率的提高,MOFs衍生C/LDH/rGO网状复合材料的氧化还原峰强度逐渐降低,表明溶液中的离子还未来得及进入电极内电化学反应已经完成。为了更好地理解这种复合材料的储能机理,其电化学分析测试结果如图4c~f所示。可以看出,电极的电荷存储过程包含两部分:电容控制部分(包括双电层电容和高度表面局域的赝电容)和扩散控制部分(基于扩散/插层的赝电容)[24]。根据方程

I=k1v+k2v1/2
Iv1/2=k1v1/2+k2

图4

图4   用MOFs衍生C/LDH/rGO网状复合材料组装成的锌离子电容器

Fig.4   Zinc ion capacitor assembled by MOFs derived C /LDH /rGO network composite materials

(a) Reaction process simulation diagram, (b) CV curves under different scanning rate, (c) Capacitance contribution CV curve at a scanning rate of 5 mV/s, (d) The proportion of surface-controlled capacitance contribution and diffusion-controlled contribution at different scanning rates, (e) CP curves at different current densities, (f) The relationship between electrode specific capacity and current densities


和不同扫描速率的CV曲线可计算电容贡献 [25]。两个方程中的I(mA)为固定电位下的电流,v(mV/s)为扫描速率,k1vk2v1∕2分别为电容贡献和扩散贡献。 式(3)中不同电位下的I/v1/2v1/2近似呈线性关系,由不同电位[21]下的斜率(k1)和扫描速率(v)可计算电容贡献(k1v)。图4c给出了扫描速率为5 mV/s时复合材料电极中扩散控制部分和电容控制部分的贡献。根据面积积分计算出电容贡献比例为34.50%、扩散贡献为65.50%。在不同扫描速率下两种机制的贡献率如图4d所示。在扫描速率为5~50 mV/s的过程中,电容的贡献从34.50%增加到82.20%。这表明,在低扫速,这种复合材料电极的扩散贡献大于电容贡献;扫速提高后,扩散贡献小于电容贡献。图4e给出了电流密度变化时复合材料的CP图。可以看出,电流密度较低时放电时间较长,随着电流密度的提高放电时间逐渐缩短。充放电曲线有一平台,与CV法测试中的氧化还原峰对应,是充放电时离子的嵌入脱出反应所致。图4f给出了电极比容量随着电流密度的变化。可以看出,随着电流密度的提高比容量呈减小的趋势,电流密度为1.0 A·g-1时的比电容最大(达到248 F·g-1),远大于rGO的比容量数值142 F·g-1 (图5a)。这可能与MOFs衍生C/LDH/rGO网状复合材料的结构有关。该结构中MOFs衍生C/LDH提供了更多活性位点,使赝电容容量提高;rGO网状结构提供了更多的离子传输通道,使倍率性能提高。图5b为用MOFs衍生C/LDH/rGO网状复合材料和rGO分别组装的锌离子电容器的循环寿命图。可以看出,用两个材料组装的锌离子电容器循环1500次后容量分别保留97.1%与99.6%,表明MOFs衍生C/LDH具有高容量的同时,循环寿命比较高。图5c给出了用MOFs衍生C/LDH/rGO网状复合材料组装的锌离子电容器的EIS曲线。可以看出,该曲线由位于高频区的半圆与位于低频区的直线组成,半圆与横轴的截距代表锌离子电容器等效内阻(Rs)。从图5c中的插图可见,该电容器的等效内阻约为5 Ω。图中低频区域线的斜率对应Warburg阻抗(W),与电极中电解质离子的扩散有关,斜率越大意味着扩散电阻越低。图中接近垂直的斜率表明组装的锌离子电容器保留了电容材料离子快速转移的优势。

图5

图5   用MOFs衍生C/LDH/rGO网状复合材料和rGO分别组装的锌离子电容器性能的对比

Fig.5   Comparison of zinc ion capacitors assembled by MOFs derived C/LDH/rGO network composite materials and rGO

(a) CP curves of two devices (current density of 1 A/g), (b) Cycle life diagram of two devices, (c) EIS curves of zinc ion capacitors assembled by MOFs derived C/LDH/rGO network composite materials


3 结论

用液相法结合煅烧可制备MOFs衍生C/ZIF-67,再用质子刻蚀可制备MOFs衍生C/Ni-Co LDH粒子,用水热辅助冻干法可制备MOFs衍生C/LDH/rGO网状复合材料。用该材料组装的锌离子电容器循环1500次后其电容保留率仍高达97.1%。其原因是:MOFs衍生C/LDH/rGO网状复合材料的网状结构具有自支撑特性,能为电解液离子提供更多的传输通道和赝电容活性位点,其电容量可达248 F·g-1

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Supercapacitors, also called ultracapacitors or electrochemical capacitors, store electrical charge on high-surface-area conducting materials. Their widespread use is limited by their low energy storage density and relatively high effective series resistance. Using chemical activation of exfoliated graphite oxide, we synthesized a porous carbon with a Brunauer-Emmett-Teller surface area of up to 3100 square meters per gram, a high electrical conductivity, and a low oxygen and hydrogen content. This sp(2)-bonded carbon has a continuous three-dimensional network of highly curved, atom-thick walls that form primarily 0.6- to 5-nanometer-width pores. Two-electrode supercapacitor cells constructed with this carbon yielded high values of gravimetric capacitance and energy density with organic and ionic liquid electrolytes. The processes used to make this carbon are readily scalable to industrial levels.

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Electrochemical capacitors, also called supercapacitors, store energy using either ion adsorption (electrochemical double layer capacitors) or fast surface redox reactions (pseudo-capacitors). They can complement or replace batteries in electrical energy storage and harvesting applications, when high power delivery or uptake is needed. A notable improvement in performance has been achieved through recent advances in understanding charge storage mechanisms and the development of advanced nanostructured materials. The discovery that ion desolvation occurs in pores smaller than the solvated ions has led to higher capacitance for electrochemical double layer capacitors using carbon electrodes with subnanometre pores, and opened the door to designing high-energy density devices using a variety of electrolytes. Combination of pseudo-capacitive nanomaterials, including oxides, nitrides and polymers, with the latest generation of nanostructured lithium electrodes has brought the energy density of electrochemical capacitors closer to that of batteries. The use of carbon nanotubes has further advanced micro-electrochemical capacitors, enabling flexible and adaptable devices to be made. Mathematical modelling and simulation will be the key to success in designing tomorrow's high-energy and high-power devices.

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Capacitive energy storage is distinguished from other types of electrochemical energy storage by short charging times and the ability to deliver significantly more power than batteries. A key limitation to this technology is its low energy density and for this reason there is considerable interest in exploring pseudocapacitive materials where faradaic mechanisms offer increased levels of energy storage. Here we show that the capacitive charge-storage properties of mesoporous films of iso-oriented alpha-MoO(3) are superior to those of either mesoporous amorphous material or non-porous crystalline MoO(3). Whereas both crystalline and amorphous mesoporous materials show redox pseudocapacitance, the iso-oriented layered crystalline domains enable lithium ions to be inserted into the van der Waals gaps of the alpha-MoO(3). We propose that this extra contribution arises from an intercalation pseudocapacitance, which occurs on the same timescale as redox pseudocapacitance. The result is increased charge-storage capacity without compromising charge/discharge kinetics in mesoporous crystalline MoO(3).

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