As an important component of alkali metal ion batteries, the anode has a huge impact on the performance of the batteries. Traditional anode such as graphene are difficult to meet the future demand for energy storage due to their low specific capacity. Therefore, it is crucial to find anode materials with high specific capacity, excellent cycling performance and stability performance. Quantum dots are widely used for compositing with anode due to their fine size and huge specific surface areas. This anode composite with quantum dot structure shows excellent electrochemical performance in alkali metal ion batteries. However, there is a lack of review and outlook on the research of quantum dots and their composites for the anode of alkali metal ion batteries. In this paper, six aspects of quantum dots, namely, metal oxide quantum dots, metal sulfide quantum dots, metal nitride quantum dots, carbon quantum dots, monolithic quantum dots and other types of quantum dots for alkali metal ion batteries are reviewed. They are focused on the mechanism of action and electrochemical properties of various types of quantum dots for composite materials. Quantum dot composite anode materials can effectively shorten the diffusion path of alkali metal ions, provide more active sites and have higher cycle stability, and are expected to become the most promising anode materials for alkali metal ion batteries. Besides, this paper analyze the problems of quantum dot anode composites, and also make an outlook on the future development of quantum dots and their composites in the field of batteries: ① Optimize quantum dots synthesis path; ② Clarify the mechanism of action of quantum dots; ③ Reduce side effect; ④ Select more suitable host materials.
Keywords：alkali metal ion batteries
;
quantum dots
;
anode
;
composite materials
;
electrochemical performance
ZHOU Junlong. Advances in the research of quantum dots anode for alkali metal ion batteries[J]. Energy Storage Science and Technology, 2023, 12(5): 1392-1408
图2
(a) MQDC-SnO2/RGO的合成示意图[32]；(b) 柔性ZnO@NPCF的合成示意图[37]；(c) NP CoO x QDs/C负极的锂化作用示意图[41]；(d) Ga2O3-QD@NC电极的锂化/脱锂过程示意图[42]
Fig. 2
(a) Schematic of the synthesis route of MQDC-SnO2/RGO[32]; (b) Schematic illustration of the fabrication process of flexible ZnO@NPCF[37]; (c) Schematic illustration of lithiation for NP CoO x QDs/C anodes[41]; (d) Chematic diagram of the lithiation/delithiation process of the Ga2O3-QD@NC electrode[42]
其他的金属氧化物与SnO2和ZnO类似，都存在体积膨胀、电导率低等问题[39-40]。缩小氧化物尺寸至量子点级并与基体材料复合能有效解决上述问题。Lu等[41]通过沉淀法制备了CoO x (CoO和Co3O4)量子点和沸石咪唑盐骨架-67-衍生碳三维复合材料(NP CoO x QDs/C)。如图2(c)所示，CoO x 量子点提高NP CoO x QDs/C的电导率并缩短Li+的传输路径从而提高了电池的倍率性能。同时，CoO x 量子点被牢牢锚定在碳基材料上，这有利于抑制CoO x 在整个循环过程中的团聚和体积变化，从而提高电池的循环性能。该电极在电流密度为1000 mA/g的条件下循环900次后的比容量仍然有1246 mAh/g。类似地，Wang等[42]通过盐酸多巴胺与Ga2O3的水热反应将Ga2O3量子点成功分散在无定形碳的内部，形成了具有特殊结构的复合物(Ga2O3-QD@NC)。碳层的存在可作为Li+快速转移的通道并提供额外的比容量。图2(d)显示出Ga2O3-QD@NC电极的锂化/脱锂过程。在锂化的过程中，Li+通过碳层运输并大量聚集在Ga2O3量子点周围，与量子点反应生成Li x Ga和LiO2。脱锂时，Li+则从量子点周围脱离，Li x Ga分解为Li+和Ga2O3量子点，此时Li+再次穿过碳层向正极移动。这种高度可逆行为使Ga2O3-QD@NC电极表现出优异的电化学性能，其初始放电比容量为1580 mAh/g，首次库仑效率达到62.8%，并且在0.1 A/g条件下循环100次后比容量保持在953 mAh/g，这一性能显著高于其他同类文献。除了碳基材料，其他基体材料也可与金属氧化物量子点复合。Huang等[43]选用笼状硅作为负极基体与低体积膨胀率(<4%)的TiO2量子点复合，有效减少了TiO2量子点的团聚。Si纳米笼具有大量的孔结构，不仅可以促进电解质传输和Li+的扩散，还可以充当电解质的存储结构从而加速电池内的氧化还原反应。同时，具有半开放结构的Si纳米笼也减少了电解质与电极不利的接触面积。这种特殊的结构将会极大提高材料的电化学性能，在1 A/g的电流密度下循环500次仍能保持616.3 mAh/g的高可逆比容量。此外，Fe3O4[44]、MnO[45]、Nb2O5[46]等金属氧化物量子点在碱金属离子电池负极材料中均取得了不错的进展。
Fang等[54]受地球通过地质板块运动释放内部应力以保持结构稳定性的启发，提出了一种滑动策略来减小充放电循环过程中体积变化。他们通过溶剂热法将ZnS量子点均匀分散在相互交织重叠的纳米片上，合成了具有分层结构的复合材料[如图3(a)所示，ZnS-QDs@mNC]，该材料可以通过锂化/脱锂过程中的滑动行为有效适应体积变化。如图3(b)所示，在锂化的过程中，ZnS量子点的各向同性膨胀可以有效吸收体积变化的应力，同时碳纳米片的滑移可利用纳米片间的间隙适应ZnS量子点的体积变化，这种滑动行为使ZnS-QDs@mNC负极的体积膨胀仅有6.5%。Shin等[55]通过静电纺丝、硫化和热蒸发成功将1T-WS2量子点嵌入多层中空毛细管束碳纳米纤维。如图3(c)所示，PNCFs上的1T-WS2量子点能够提供丰富的锂存储位点，中空的毛细管束能够缩短Li+的通道，提高Li+的扩散速率，同时由于1T-WS2被固定在PNCFs上，其在锂化和脱锂过程中的体积膨胀得到抑制。从而使该负极材料在充放电过程中表现出较高的比容量(100 mA/g下循环100次后比容量为716.5 mAh/g)、优异的倍率性能和循环稳定性(528.1 mAh/g下循环1000次后容量保持率为87.8%)。此外，Guo等[56]利用一步合成法在含N、S掺杂的超薄碳纳米片上原位形成了CoS x 量子点。碳纳米片上富集大量的N和S为钠的存储提供丰富的活性位点和较高电导率，同时超细的CoS x 量子点结构和异质结构提高了CoS x 的稳定性，从而提高了材料的离子和电子导电性。如图3(d)所示，在放电后，电极上的CoS x 量子点转化为Co纳米颗粒并形成SEI层，之后充电过程中Co纳米颗粒会催化SEI层的分解形成CoS x 量子点，这表明该电极是高度可逆的。电极表面形成的可逆SEI层不仅提高了电极初始库仑效率(94.5%)，而且提供了更多的可逆容量(约为658 mAh/g)。同时，该电极还表现出优异的倍率性能，如图3(e)所示，即使在10 A/g的高电流密度下，CoS x @NSC-1电极仍然可以保持高于500 mAh/g的可逆比容量，显著高于NSC电极。
图3
(a) ZnS-QDs@mNC的低倍率TEM图像[54]；(b) ZnS-QDs@mNC锂化前后示意图[54]；(c) WS2-PCNF10的储锂机理示意图[52]；(d) CoS x @NSC-1电极上可逆SEI层的形成示意图[55]；(e) NSC和CoS x @NSC-y电极在不同电流密度下的比容量[56]
Fig. 3
(a) Low magnification TEM image of ZnS-QDs@mNC[54]; (b) Schematic illustration of ZnS-QDs@mNC before and after lithiation[54]; (c) Schematic illustration of the three main effects on WS2-PCNF10 for boosting ultrafast lithium storage performances[55]; (d) Schematic illustration of the reversible SEI layer formation on the CoS x @NSC-1 electrode[56]; (e) Specific capacities of the NSC and CoS x @NSC-y electrodes at varied current densities[56]
Fig. 4
(a) Schematic representation of the Na+ storage mechanism for TiN/C composite anodes[61]; (b) Schematic illustration of lithiation and delithiation mechanisms for VN-bulk NPs, VN@NC NPs and VNQD@NC HSs[62]; (c) Cycling performance of VN-QDS/CM-600 at 0.5 A/g[63]; (d) TEM images of VNQD with NH4VO3[64]
Fig. 5
(a) Schematic of the structures of CDs[67]; (b) Adsorption patterns for on four ions on C24H12, two ions on C24H12, five ions on C54H18, three ions on C54H18[68]; (c) TEM images of the GQDs@CNT[69]; (d) Schematic diagrams showing the formation of the hierarchical LTO/N-GQD/Super-P structure[71]; (e) Rate capability of pristine LTO and LTO-NGQ20 electrodes from 0.2 C to 50 C[71]
Fig. 6
(a) Illustration the advantage of surface functional group-tailored BN-CQD structure[73]; (b) Schematic diagram of CDs@rGO stacked models[74]; (c) Schematic of the preparation process for LAP-rGO-CDs[75]; (d) Schematic illustration of the three main effects on the F-CQD@etched-Cu electrode for improving ultrafast cycling[78]
Fig. 7
(a) Schematics of the lithiation and subsequent delithiation process of the 3DOP Ge@N-C anode and Ge/N-C anode[79]; (b) The difference charge density of SbQD@C at the heterogeneous interface (e/Å3)[80]; (c) Proposed mechanism of the B@rGO anode during the lithium storage process; and schematic diagram of the stacked models at the cross-section[84]
Fig. 8
(a) Schematic illustration of Ni2P@NPC building-up process[88]; (b) Schematic illustration of the mechanism of the superior performance of 0D/2D SnSe@f-Ti3C2 composites[91]; (c) Li+ diffusion path of Fe2O3/MoO3@N[93]
ZHANG Z, ZHAO D C, XU Y Y, et al. A review on electrode materials of fast-charging lithium-ion batteries[J]. Chemical Record, 2022, 22(10): e202200127.
SUN C K, ZHANG X, LI C, et al. A presodiation strategy with high efficiency by utilizing low-price and eco-friendly Na2CO3 as the sacrificial salt towards high-performance pouch sodium-ion capacitors[J]. Journal of Power Sources, 2021, 515: 230628.
LIU J W, YUE M, WANG S Q, et al. A review of performance attenuation and mitigation strategies of lithium-ion batteries[J]. Advanced Functional Materials, 2022, 32(8): 2107769.
XU B, LEE J, KWON D, et al. Mitigation strategies for Li-ion battery thermal runaway: A review[J]. Renewable and Sustainable Energy Reviews, 2021, 150: 111437.
TRAN N, TA Q T H, TRAN V V. Review on the application of green and environmentally benign biowaste and natural substances in the synthesis of lithium-ion batteries[J]. International Journal of Energy Research, 2022, 46(10): 13251-13275.
BIN FAYYAZ AHSAN M, MEKHILEF S, SOON T K, et al. Lithium-ion battery and supercapacitor-based hybrid energy storage system for electric vehicle applications: A review[J]. International Journal of Energy Research, 2022, 46(14): 19826-19854.
LIU Z M, WANG J, LU B G. Plum pudding model inspired KVPO4F@3DC as high-voltage and hyperstable cathode for potassium ion batteries[J]. Science Bulletin, 2020, 65(15): 1242-1251.
LIU Z M, WANG J, DING H B, et al. Carbon nanoscrolls for aluminum battery[J]. ACS Nano, 2018, 12(8): 8456-8466.
WANG J, LIU Z M, ZHOU J, et al. Insights into metal/metalloid-based alloying anodes for potassium ion batteries[J]. ACS Materials Letters, 2021, 3(11): 1572-1598.
PARK G D, PARK J S, KIM J K, et al. Recent advances in heterostructured anode materials with multiple anions for advanced alkali-ion batteries[J]. Advanced Energy Materials, 2021, 11(27): 2003058.
BI J X, DU Z Z, SUN J M, et al. On the road to the frontiers of lithium-ion batteries: A review and outlook of graphene anodes[J]. Advanced Materials, 2023, 35(16).
QIAO Y, ZHAO H P, SHEN Y L, et al. Recycling of graphite anode from spent lithium-ion batteries: Advances and perspectives[J]. EcoMat, 2023, 5(4).
LIU Z M, WANG J, JIA X X, et al. Graphene armored with a crystal carbon shell for ultrahigh-performance potassium ion batteries and aluminum batteries[J]. ACS Nano, 2019, 13(9): 10631-10642.
JIANG L J, ZHANG S, QIAO Y, et al. A review of failure mechanisms and anode graphite recycling from spent lithium-ion batteries[J]. Energy Storage Science and Technology, 2023, 12(3): 822-834.
ARISTOTE N T, SONG Z R, DENG W T, et al. Effect of double and triple-doping of sulfur, nitrogen and phosphorus on the initial coulombic efficiency and rate performance of the biomass derived hard carbon as anode for sodium-ion batteries[J]. Journal of Power Sources, 2023, 558: 232517.
WANG S E, KIM M J, LEE J W, et al. A novel high-performance TiO2-x/TiO1-yNy coating material for silicon anode in lithium-ion batteries[J]. Small Methods, 2022, 6(7): 2200430.
SHI J W, GAO H Y, HU G X, et al. Nanostructured SiOx-based anodes synthesized by a scalable micelle assisted method for high-performance lithium-ion battery[J]. Materials Chemistry and Physics, 2022, 291: 126721.
SHI H F, ZHANG W Y, WANG J S, et al. Scalable synthesis of a porous structure silicon/carbon composite decorated with copper as an anode for lithium ion batteries[J]. Applied Surface Science, 2023, 620: 156843.
MENG D X, WEI L H, SHI J W, et al. A review of enhanced electrocatalytic composites hydrogen/oxygen evolution based on quantum dot[J]. Journal of Industrial and Engineering Chemistry, 2023, 121: 27-39.
YU Y, MA T, HUANG H. Semiconducting quantum dots for energy conversion and storage[J]. Advanced Functional Materials, 2023, 33(16): 2213770.
CHEN Y J, YU S, FAN X B, et al. Mechanistic insights into the influence of surface ligands on quantum dots for photocatalysis[J]. Journal of Materials Chemistry A, 2023, 11(16): 8497-8514.
YANG D, CUI Z J, WEN Z Q, et al. Recent updates on functionalized silicon quantum-dot-based nanoagents for biomedical applications[J]. ACS Materials Letters, 2023, 5(4): 985-1008.
HUANG K, LIU J L, YUAN J J, et al. Perovskite-quantum dot hybrid solar cells: A multi-win strategy for high performance and stability[J]. Journal of Materials Chemistry A, 2023, 11(9): 4487-4509.
WANG Y R, ZHUANG Q F, LI Y, et al. Bio-inspired synthesis of transition-metal oxide hybrid ultrathin nanosheets for enhancing the cycling stability in lithium-ion batteries[J].Nano Research, 2022, 15(6): 5064-5071.
YANG X B, WANG H Q, SONG Y Y, et al. Low-temperature synthesis of a porous high-entropy transition-metal oxide as an anode for high-performance lithium-ion batteries[J]. ACS Applied Materials & Interfaces, 2022, 14(23): 26873-26881.
CHEN Y, CHEN X Y, ZHANG Y L. A comprehensive review on metal-oxide nanocomposites for high-performance lithium-ion battery anodes[J]. Energy & Fuels, 2021, 35(8): 6420-6442.
KIM S S, JUNG S M, SENTHIL C, et al. Unlocking rapid charging and extended lifetimes for Li-ion batteries using freestanding quantum conversion-type aerofilm anode[J]. ACS Nano, 2021, 15(11): 18437-18447.
ZHU C L, ZHU S M, ZHANG K, et al. Confined SnO2 quantum-dot clusters in graphene sheets as high-performance anodes for lithium-ion batteries[J]. Scientific Reports, 2016, 6(1): 1-8.
WU C P, XIE K X, HE J P, et al. SnO2 quantum dots modified N-doped carbon as high-performance anode for lithium ion batteries by enhanced pseudocapacitance[J].Rare Metals, 2021, 40(1): 48-56.
WU K, SHI B W, QI L Y, et al. SnO2 quantum dots @ 3D sulfur-doped reduced graphene oxides as active and durable anode for lithium ion batteries[J]. Electrochimica Acta, 2018, 291: 24-30.
DONG C L, ZHANG X L, DONG W J, et al. ZnO/ZnS heterostructure with enhanced interfacial lithium absorption for robust and large-capacity energy storage[J]. Energy & Environmental Science, 2022, 15(11): 4738-4747.
FAIZAH F, PRIYONO B, CHAIRUNNISA Z E, et al. Zinc oxide nanoparticle and its characterization in the LTO/ZnO composite for lithium-ion battery anode[J]. IOP Conference Series: Materials Science and Engineering, 2021, 1098(6): 062027.
MA X, LI Z H, CHEN D K, et al. Nitrogen-doped porous carbon sponge-confined ZnO quantum dots for metal collector-free lithium ion battery[J]. Journal of Electroanalytical Chemistry, 2019, 848: 113275.
TAN Q K, KONG X L, GUAN X G, et al. Crystallization of zinc oxide quantum dots on graphene sheets as an anode material for lithium ion batteries[J]. CrystEngComm, 2020, 22(2): 320-329.
DONG X L, ZHANG Y T, CUI C S, et al. Study on the binary transition metal oxide Mn2V2O7 structures for high performance lithium-ion batteries[J]. Journal of Alloys and Compounds, 2022, 907: 164518.
ZHOU G L, DING W H, GUAN Y, et al. Progress of NiO-based anodes for high-performance Li-ion batteries[J]. The Chemical Record, 2022, 22(10): https://doi.org/10.1002/tcr.202200111.
LU D J, YUAN C, YU M C, et al. Nanoporous composites of CoOx quantum dots and ZIF-derived carbon as high-performance anodes for lithium-ion batteries[J]. ACS Omega, 2020, 5(34): 21488-21496.
WANG Y Y, XIONG Z S, ZHAO Y, et al. Ga2O3 quantum dots with N-doped amorphous carbon fixed for efficient storage and transfer of lithium ions by introduction of dopamine hydrochloride[J]. Langmuir, 2023, 39(10): 3628-3636.
HUANG Y X, LYU Y Y, ZOU Y L, et al. TiO2 quantum dots decorated Si nanocage for enhanced lithium ion batteries[J]. Journal of Electroanalytical Chemistry, 2023, 930: 117128.
LIU Y, DAI Y, JIANG X B, et al. Fe3O4 quantum dots embedded in porous carbon microspheres for long-life lithium-ion batteries[J]. Materials Today Energy, 2019, 12: 269-276.
ZHU X Q, LI J, LIU P, et al. Nitrogen-doped thermally reduced graphene oxide quantum dots-MnO composite toward enhanced-performance Li-ion battery[J]. Applied Physics A, 2018, 124(10): 722.
LIANG F H, WU D N, JIANG L, et al. Layered niobium oxide hydrate anode with excellent performance for lithium-ion batteries[J]. ACS Applied Materials & Interfaces, 2021, 13(43): 51057-51065.
WANG S C, QU C W, WEN J W, et al. Progress of transition metal sulfides used as lithium-ion battery anodes[J]. Materials Chemistry Frontiers, 2023: https://doi.org/10.1039/D2QM01200F.
ZHOU X H, SU K M, KANG W M, et al. Locking metal sulfide nanoparticles in interconnected porous carbon nanofibers with protective macro-porous skin as freestanding anodes for lithium ion batteries[J]. Chemical Engineering Journal, 2020, 397: 125271.
ZHANG B, XU B, XIAO Z, et al. Inner-stress-dissipative, rapid self-healing core-shell sulfide quantum dots for remarkable potassium-ion storage[J]. Energy Storage Materials, 2023, 56: 96-107.
ZHAO J B, ZHANG Y Y, WANG Y H, et al. The application of nanostructured transition metal sulfides as anodes for lithium ion batteries[J]. Journal of Energy Chemistry, 2018, 27(6): 1536-1554.
XU G B, YANG L W, WEI X L, et al. MoS2-quantum-dot-interspersed Li4Ti5O12 nanosheets with enhanced performance for li-and Na-ion batteries[J]. Advanced Functional Materials, 2016, 26(19): 3349-3358.
VEERASUBRAMANI G K, PARK M S, CHOI J Y, et al. Ultrasmall SnS quantum dots anchored onto nitrogen-enriched carbon nanospheres as an advanced anode material for sodium-ion batteries[J]. ACS Applied Materials & Interfaces, 2020, 12(6): 7114-7124.
KE G X, CHEN H H, HE J, et al. Ultrathin MoS2 anchored on 3D carbon skeleton containing SnS quantum dots as a high-performance anode for advanced lithium ion batteries[J]. Chemical Engineering Journal, 2021, 403: 126251.
FANG D L, CHEN S M, WANG X, et al. ZnS quantum dots@multilayered carbon: Geological-plate-movement-inspired design for high-energy Li-ion batteries[J]. Journal of Materials Chemistry A, 2018, 6(18): 8358-8365.
SHIN D Y, LEE J S, KOO B R, et al. Hierarchical hybrid nanostructure of 1T-tungsten disulfide quantum dots/multihollow capillary bundle-type mesoporous carbon for ultrafast and ultrastable lithium storage[J]. Chemical Engineering Journal, 2021, 412: 128547.
GUO Q B, MA Y F, CHEN T T, et al. Cobalt sulfide quantum dot embedded N/S-doped carbon nanosheets with superior reversibility and rate capability for sodium-ion batteries[J]. ACS Nano, 2017, 11(12): 12658-12667.
WANG P Y, ZHAO B C, BAI J, et al. Transition metal nitrides in lithium-and sodium-ion batteries: Recent progress and perspectives[J]. Advanced Materials Interfaces, 2022, 9(24): 2200606.
LIU R J, YANG L X, ZHANG T Y, et al. Nano-sheet and nano-laminar vanadium nitride as anodes for high-performance lithium-ions storage[J]. International Journal of Energy Research, 2022, 46(15): 22486-22500.
YI H, HUANG Y, SHA Z C, et al. Facile synthesis of Mo2N quantum dots embedded N-doped carbon nanosheets composite as advanced anode materials for lithium-ion batteries[J]. Materials Letters, 2020, 276: 128205.
LIU C X, WANG C, MENG X W, et al. Tungsten nitride nanoparticles anchored on porous borocarbonitride as high-rate anode for lithium ion batteries[J]. Chemical Engineering Journal, 2020, 399: 125705.
LIU M, ZHANG Z L, XIE Y Y, et al. Titanium nitride as a promising sodium-ion battery anode: Interface-confined preparation and electrochemical investigation[J]. Dalton Transactions, 2022, 51(34): 12855-12865.
YUAN J, HU X, CHEN J X, et al. Insitu formation of vanadium nitride quantum dots on N-doped carbon hollow spheres for superior lithium and sodium storage[J]. Journal of Materials Chemistry A, 2019, 7(15): 9289-9296.
WU H Y, YU Q Y, LAO C Y, et al. Scalable synthesis of VN quantum dots encapsulated in ultralarge pillared N-doped mesoporous carbon microsheets for superior potassium storage[J]. Energy Storage Materials, 2019, 18: 43-50.
YUAN S, LAI Q H, DUAN X, et al. Carbon-based materials as anode materials for lithium-ion batteries and lithium-ion capacitors: A review[J]. Journal of Energy Storage, 2023, 61: 106716.
YUAN X, LI H J, BAI W H, et al. Application of biomass-derived carbon-based anode materials in sodium ion battery[J]. Energy Storage Science and Technology, 2023, 12(3): 721-742.
PATTARAPONGDILOK N, PARASUK V. Adsorptions of lithium ion/atom and packing of Li ions on graphene quantum dots: Application for Li-ion battery[J]. Computational and Theoretical Chemistry, 2020, 1177: 112779.
ZHAO X W, WU Y Z, WANG Y S, et al. High-performance Li-ion batteries based on graphene quantum dot wrapped carbon nanotube hybrid anodes[J].Nano Research, 2020, 13(4): 1044-1052.
YU H, ZHU W J, ZHOU H, et al. Porous carbon derived from metal-organic framework@graphene quantum dots as electrode materials for supercapacitors and lithium-ion batteries[J]. RSC Advances, 2019, 9(17): 9577-9583.
KHAN F, OH M, KIM J H. N-functionalized graphene quantum dots: Charge transporting layer for high-rate and durable Li4Ti5O12-based Li-ion battery[J]. Chemical Engineering Journal, 2019, 369: 1024-1033.
VIJAYA KUMAR SAROJA A P, GARAPATI M S, SHYIAMALADEVI R, et al. Facile synthesis of heteroatom doped and undoped graphene quantum dots as active materials for reversible lithium and sodium ions storage[J]. Applied Surface Science, 2020, 504: 144430.
KIM K H, AHN H J. Surface functional group-tailored B and N co-doped carbon quantum dot anode for lithium-ion batteries[J]. International Journal of Energy Research, 2022, 46(6): 8367-8375.
ZHANG E J, JIA X X, WANG B, et al. Carbon dots@rGO paper as freestanding and flexible potassium-ion batteries anode[J]. Advanced Science, 2020, 7(15): 2000470.
DONG S, SONG Y L, FANG Y Z, et al. Microwave-assisted synthesis of carbon dots modified graphene for full carbon-based potassium ion capacitors[J]. Carbon, 2021, 178: 1-9.
JAVED M, SAQIB A N S, ATA-UR-REHMAN, et al. Carbon quantum dots from glucose oxidation as a highly competent anode material for lithium and sodium-ion batteries[J]. Electrochimica Acta, 2019, 297: 250-257.
KRAJEWSKI M, CHEN C H, HUANG Z T, et al. Li4Ti5O12 coated by biomass-derived carbon quantum dots as anode material with enhanced electrochemical performance for lithium-ion batteries[J]. Energies, 2022, 15(20): 7715.
SHIN D Y, SUNG K W, AHN H J. Fluorine-doped carbon quantum dot interfacial layer on stockade-like etched copper foil for boosting Li-ion storage[J]. Chemical Engineering Journal, 2021, 413: 127563.
WANG Y, LUO S N, CHEN M, et al. Uniformly confined germanium quantum dots in 3D ordered porous carbon framework for high-performance Li-ion battery[J]. Advanced Functional Materials, 2020, 30(16): 2000373.
QIU T Y, YANG L, XIANG Y E, et al. Heterogeneous interface design for enhanced sodium storage: Sb quantum dots confined by functional carbon[J]. Small Methods, 2021, 5(7): 2100188.
CHOI Y H, PARK H, LEE S, et al. Synthesis and electrochemical performance of π-conjugated molecule bridged silicon quantum dot cluster as anode material for lithium-ion batteries[J]. ACS Omega, 2020, 5(15): 8629-8637.
HU W, HE K, WU S, et al. Ordered sandwich silicon quantum dot/Fe3O4/reduced graphene oxide architectures for high-performance lithium-ion batteries[J]. Journal of Alloys and Compounds, 2023, 943: 168947.
ZHANG G H, ZHU J, ZENG W, et al. Tin quantum dots embedded in nitrogen-doped carbon nanofibers as excellent anode for lithium-ion batteries[J]. Nano Energy, 2014, 9: 61-70.
WANG H Q, AN D, TIAN P Z, et al. Incorporating quantum-sized boron dots into 3D cross-linked rGO skeleton to enable the activity of boron anode for favorable lithium storage[J]. Chemical Engineering Journal, 2021, 425: 130659.
GE H, CUI L X, ZHANG B, et al. Ag quantum dots promoted Li4Ti5O12/TiO2 nanosheets with ultrahigh reversible capacity and super rate performance for power lithium-ion batteries[J]. Journal of Materials Chemistry A, 2016, 4(43): 16886-16895.
WANG D, ZHOU J S, LI J K, et al. Cobalt-boron nanoparticles anchored on graphene as anode of lithium ion batteries[J]. Chemical Engineering Journal, 2019, 360: 271-279.
WANG S, ZHANG X B. N-doped C@Zn3B2O6 as a low cost and environmentally friendly anode material for Na-ion batteries: High performance and new reaction mechanism[J]. Advanced Materials, 2019, 31(5): 1805432.
YAN Z H, HUANG Z Y, YAO Y, et al. Monodispersed Ni2P nanodots embedded in N, P co-doped porous carbon as super stable anode material for potassium-ion batteries[J]. Journal of Alloys and Compounds, 2021, 858: 158203.
YAN Z H, HUANG Z Y, ZHOU H H, et al. Facile fabrication of MoP nanodots embedded in porous carbon as excellent anode material for potassium-ion batteries[J]. Journal of Energy Chemistry, 2021, 54: 571-578.
WANG M S, PENG A M, XU H, et al. Amorphóus SnSe quantum dots anchoring on graphene as high performance anodes for battery/capacitor sodium ion storage[J]. Journal of Power Sources, 2020, 469: 228414.
NI G X, ZHANG Y J, LI Y Z, et al. SnSe quantum dots anchored on few-layered Ti3C2 as anodes for sodium ion batteries with enhanced cycling stability[J]. New Journal of Chemistry, 2023, 47(14): 6540-6550.
LIU W, YUAN J J, HAO Y C, et al. Heterogeneous structured MoSe2-MoO3 quantum dots with enhanced sodium/potassium storage[J]. Journal of Materials Chemistry A, 2020, 8(44): 23395-23403.
DING J, SHENG R, ZHANG Y, et al. Fe2O3/MoO3@NG heterostructure enables high pseudocapacitance and fast electrochemical reaction kinetics for lithium-ion batteries[J]. ACS Applied Materials & Interfaces, 2022, 14(33): 37747-37758.
... [32]；(b) 柔性ZnO@NPCF的合成示意图[37]；(c) NP CoO x QDs/C负极的锂化作用示意图[41]；(d) Ga2O3-QD@NC电极的锂化/脱锂过程示意图[42](a) Schematic of the synthesis route of MQDC-SnO<sub>2</sub>/RGO<sup>[<xref ref-type="bibr" rid="R32">32</xref>]</sup>; (b) Schematic illustration of the fabrication process of flexible ZnO@NPCF<sup>[<xref ref-type="bibr" rid="R37">37</xref>]</sup>; (c) Schematic illustration of lithiation for NP CoO <i><sub>x</sub></i> QDs/C anodes<sup>[<xref ref-type="bibr" rid="R41">41</xref>]</sup>; (d) Chematic diagram of the lithiation/delithiation process of the Ga<sub>2</sub>O<sub>3</sub>-QD@NC electrode<sup>[<xref ref-type="bibr" rid="R42">42</xref>]</sup>Fig. 2
... [32]; (b) Schematic illustration of the fabrication process of flexible ZnO@NPCF[37]; (c) Schematic illustration of lithiation for NP CoO x QDs/C anodes[41]; (d) Chematic diagram of the lithiation/delithiation process of the Ga2O3-QD@NC electrode[42]Fig. 2
(a) Schematic of the synthesis route of MQDC-SnO<sub>2</sub>/RGO<sup>[<xref ref-type="bibr" rid="R32">32</xref>]</sup>; (b) Schematic illustration of the fabrication process of flexible ZnO@NPCF<sup>[<xref ref-type="bibr" rid="R37">37</xref>]</sup>; (c) Schematic illustration of lithiation for NP CoO <i><sub>x</sub></i> QDs/C anodes<sup>[<xref ref-type="bibr" rid="R41">41</xref>]</sup>; (d) Chematic diagram of the lithiation/delithiation process of the Ga<sub>2</sub>O<sub>3</sub>-QD@NC electrode<sup>[<xref ref-type="bibr" rid="R42">42</xref>]</sup>Fig. 2
... [37]; (c) Schematic illustration of lithiation for NP CoO x QDs/C anodes[41]; (d) Chematic diagram of the lithiation/delithiation process of the Ga2O3-QD@NC electrode[42]Fig. 2
... 其他的金属氧化物与SnO2和ZnO类似，都存在体积膨胀、电导率低等问题[39-40].缩小氧化物尺寸至量子点级并与基体材料复合能有效解决上述问题.Lu等[41]通过沉淀法制备了CoO x (CoO和Co3O4)量子点和沸石咪唑盐骨架-67-衍生碳三维复合材料(NP CoO x QDs/C).如图2(c)所示，CoO x 量子点提高NP CoO x QDs/C的电导率并缩短Li+的传输路径从而提高了电池的倍率性能.同时，CoO x 量子点被牢牢锚定在碳基材料上，这有利于抑制CoO x 在整个循环过程中的团聚和体积变化，从而提高电池的循环性能.该电极在电流密度为1000 mA/g的条件下循环900次后的比容量仍然有1246 mAh/g.类似地，Wang等[42]通过盐酸多巴胺与Ga2O3的水热反应将Ga2O3量子点成功分散在无定形碳的内部，形成了具有特殊结构的复合物(Ga2O3-QD@NC).碳层的存在可作为Li+快速转移的通道并提供额外的比容量.图2(d)显示出Ga2O3-QD@NC电极的锂化/脱锂过程.在锂化的过程中，Li+通过碳层运输并大量聚集在Ga2O3量子点周围，与量子点反应生成Li x Ga和LiO2.脱锂时，Li+则从量子点周围脱离，Li x Ga分解为Li+和Ga2O3量子点，此时Li+再次穿过碳层向正极移动.这种高度可逆行为使Ga2O3-QD@NC电极表现出优异的电化学性能，其初始放电比容量为1580 mAh/g，首次库仑效率达到62.8%，并且在0.1 A/g条件下循环100次后比容量保持在953 mAh/g，这一性能显著高于其他同类文献.除了碳基材料，其他基体材料也可与金属氧化物量子点复合.Huang等[43]选用笼状硅作为负极基体与低体积膨胀率(<4%)的TiO2量子点复合，有效减少了TiO2量子点的团聚.Si纳米笼具有大量的孔结构，不仅可以促进电解质传输和Li+的扩散，还可以充当电解质的存储结构从而加速电池内的氧化还原反应.同时，具有半开放结构的Si纳米笼也减少了电解质与电极不利的接触面积.这种特殊的结构将会极大提高材料的电化学性能，在1 A/g的电流密度下循环500次仍能保持616.3 mAh/g的高可逆比容量.此外，Fe3O4[44]、MnO[45]、Nb2O5[46]等金属氧化物量子点在碱金属离子电池负极材料中均取得了不错的进展. ...
... Electrochemical properties of quantum dots and their composite materialsTable 1
... 其他的金属氧化物与SnO2和ZnO类似，都存在体积膨胀、电导率低等问题[39-40].缩小氧化物尺寸至量子点级并与基体材料复合能有效解决上述问题.Lu等[41]通过沉淀法制备了CoO x (CoO和Co3O4)量子点和沸石咪唑盐骨架-67-衍生碳三维复合材料(NP CoO x QDs/C).如图2(c)所示，CoO x 量子点提高NP CoO x QDs/C的电导率并缩短Li+的传输路径从而提高了电池的倍率性能.同时，CoO x 量子点被牢牢锚定在碳基材料上，这有利于抑制CoO x 在整个循环过程中的团聚和体积变化，从而提高电池的循环性能.该电极在电流密度为1000 mA/g的条件下循环900次后的比容量仍然有1246 mAh/g.类似地，Wang等[42]通过盐酸多巴胺与Ga2O3的水热反应将Ga2O3量子点成功分散在无定形碳的内部，形成了具有特殊结构的复合物(Ga2O3-QD@NC).碳层的存在可作为Li+快速转移的通道并提供额外的比容量.图2(d)显示出Ga2O3-QD@NC电极的锂化/脱锂过程.在锂化的过程中，Li+通过碳层运输并大量聚集在Ga2O3量子点周围，与量子点反应生成Li x Ga和LiO2.脱锂时，Li+则从量子点周围脱离，Li x Ga分解为Li+和Ga2O3量子点，此时Li+再次穿过碳层向正极移动.这种高度可逆行为使Ga2O3-QD@NC电极表现出优异的电化学性能，其初始放电比容量为1580 mAh/g，首次库仑效率达到62.8%，并且在0.1 A/g条件下循环100次后比容量保持在953 mAh/g，这一性能显著高于其他同类文献.除了碳基材料，其他基体材料也可与金属氧化物量子点复合.Huang等[43]选用笼状硅作为负极基体与低体积膨胀率(<4%)的TiO2量子点复合，有效减少了TiO2量子点的团聚.Si纳米笼具有大量的孔结构，不仅可以促进电解质传输和Li+的扩散，还可以充当电解质的存储结构从而加速电池内的氧化还原反应.同时，具有半开放结构的Si纳米笼也减少了电解质与电极不利的接触面积.这种特殊的结构将会极大提高材料的电化学性能，在1 A/g的电流密度下循环500次仍能保持616.3 mAh/g的高可逆比容量.此外，Fe3O4[44]、MnO[45]、Nb2O5[46]等金属氧化物量子点在碱金属离子电池负极材料中均取得了不错的进展. ...
... Electrochemical properties of quantum dots and their composite materialsTable 1
(a) Schematic of the synthesis route of MQDC-SnO<sub>2</sub>/RGO<sup>[<xref ref-type="bibr" rid="R32">32</xref>]</sup>; (b) Schematic illustration of the fabrication process of flexible ZnO@NPCF<sup>[<xref ref-type="bibr" rid="R37">37</xref>]</sup>; (c) Schematic illustration of lithiation for NP CoO <i><sub>x</sub></i> QDs/C anodes<sup>[<xref ref-type="bibr" rid="R41">41</xref>]</sup>; (d) Chematic diagram of the lithiation/delithiation process of the Ga<sub>2</sub>O<sub>3</sub>-QD@NC electrode<sup>[<xref ref-type="bibr" rid="R42">42</xref>]</sup>Fig. 2
... 其他的金属氧化物与SnO2和ZnO类似，都存在体积膨胀、电导率低等问题[39-40].缩小氧化物尺寸至量子点级并与基体材料复合能有效解决上述问题.Lu等[41]通过沉淀法制备了CoO x (CoO和Co3O4)量子点和沸石咪唑盐骨架-67-衍生碳三维复合材料(NP CoO x QDs/C).如图2(c)所示，CoO x 量子点提高NP CoO x QDs/C的电导率并缩短Li+的传输路径从而提高了电池的倍率性能.同时，CoO x 量子点被牢牢锚定在碳基材料上，这有利于抑制CoO x 在整个循环过程中的团聚和体积变化，从而提高电池的循环性能.该电极在电流密度为1000 mA/g的条件下循环900次后的比容量仍然有1246 mAh/g.类似地，Wang等[42]通过盐酸多巴胺与Ga2O3的水热反应将Ga2O3量子点成功分散在无定形碳的内部，形成了具有特殊结构的复合物(Ga2O3-QD@NC).碳层的存在可作为Li+快速转移的通道并提供额外的比容量.图2(d)显示出Ga2O3-QD@NC电极的锂化/脱锂过程.在锂化的过程中，Li+通过碳层运输并大量聚集在Ga2O3量子点周围，与量子点反应生成Li x Ga和LiO2.脱锂时，Li+则从量子点周围脱离，Li x Ga分解为Li+和Ga2O3量子点，此时Li+再次穿过碳层向正极移动.这种高度可逆行为使Ga2O3-QD@NC电极表现出优异的电化学性能，其初始放电比容量为1580 mAh/g，首次库仑效率达到62.8%，并且在0.1 A/g条件下循环100次后比容量保持在953 mAh/g，这一性能显著高于其他同类文献.除了碳基材料，其他基体材料也可与金属氧化物量子点复合.Huang等[43]选用笼状硅作为负极基体与低体积膨胀率(<4%)的TiO2量子点复合，有效减少了TiO2量子点的团聚.Si纳米笼具有大量的孔结构，不仅可以促进电解质传输和Li+的扩散，还可以充当电解质的存储结构从而加速电池内的氧化还原反应.同时，具有半开放结构的Si纳米笼也减少了电解质与电极不利的接触面积.这种特殊的结构将会极大提高材料的电化学性能，在1 A/g的电流密度下循环500次仍能保持616.3 mAh/g的高可逆比容量.此外，Fe3O4[44]、MnO[45]、Nb2O5[46]等金属氧化物量子点在碱金属离子电池负极材料中均取得了不错的进展. ...
(a) Schematic of the synthesis route of MQDC-SnO<sub>2</sub>/RGO<sup>[<xref ref-type="bibr" rid="R32">32</xref>]</sup>; (b) Schematic illustration of the fabrication process of flexible ZnO@NPCF<sup>[<xref ref-type="bibr" rid="R37">37</xref>]</sup>; (c) Schematic illustration of lithiation for NP CoO <i><sub>x</sub></i> QDs/C anodes<sup>[<xref ref-type="bibr" rid="R41">41</xref>]</sup>; (d) Chematic diagram of the lithiation/delithiation process of the Ga<sub>2</sub>O<sub>3</sub>-QD@NC electrode<sup>[<xref ref-type="bibr" rid="R42">42</xref>]</sup>Fig. 2
... 其他的金属氧化物与SnO2和ZnO类似，都存在体积膨胀、电导率低等问题[39-40].缩小氧化物尺寸至量子点级并与基体材料复合能有效解决上述问题.Lu等[41]通过沉淀法制备了CoO x (CoO和Co3O4)量子点和沸石咪唑盐骨架-67-衍生碳三维复合材料(NP CoO x QDs/C).如图2(c)所示，CoO x 量子点提高NP CoO x QDs/C的电导率并缩短Li+的传输路径从而提高了电池的倍率性能.同时，CoO x 量子点被牢牢锚定在碳基材料上，这有利于抑制CoO x 在整个循环过程中的团聚和体积变化，从而提高电池的循环性能.该电极在电流密度为1000 mA/g的条件下循环900次后的比容量仍然有1246 mAh/g.类似地，Wang等[42]通过盐酸多巴胺与Ga2O3的水热反应将Ga2O3量子点成功分散在无定形碳的内部，形成了具有特殊结构的复合物(Ga2O3-QD@NC).碳层的存在可作为Li+快速转移的通道并提供额外的比容量.图2(d)显示出Ga2O3-QD@NC电极的锂化/脱锂过程.在锂化的过程中，Li+通过碳层运输并大量聚集在Ga2O3量子点周围，与量子点反应生成Li x Ga和LiO2.脱锂时，Li+则从量子点周围脱离，Li x Ga分解为Li+和Ga2O3量子点，此时Li+再次穿过碳层向正极移动.这种高度可逆行为使Ga2O3-QD@NC电极表现出优异的电化学性能，其初始放电比容量为1580 mAh/g，首次库仑效率达到62.8%，并且在0.1 A/g条件下循环100次后比容量保持在953 mAh/g，这一性能显著高于其他同类文献.除了碳基材料，其他基体材料也可与金属氧化物量子点复合.Huang等[43]选用笼状硅作为负极基体与低体积膨胀率(<4%)的TiO2量子点复合，有效减少了TiO2量子点的团聚.Si纳米笼具有大量的孔结构，不仅可以促进电解质传输和Li+的扩散，还可以充当电解质的存储结构从而加速电池内的氧化还原反应.同时，具有半开放结构的Si纳米笼也减少了电解质与电极不利的接触面积.这种特殊的结构将会极大提高材料的电化学性能，在1 A/g的电流密度下循环500次仍能保持616.3 mAh/g的高可逆比容量.此外，Fe3O4[44]、MnO[45]、Nb2O5[46]等金属氧化物量子点在碱金属离子电池负极材料中均取得了不错的进展. ...
... Electrochemical properties of quantum dots and their composite materialsTable 1
... 其他的金属氧化物与SnO2和ZnO类似，都存在体积膨胀、电导率低等问题[39-40].缩小氧化物尺寸至量子点级并与基体材料复合能有效解决上述问题.Lu等[41]通过沉淀法制备了CoO x (CoO和Co3O4)量子点和沸石咪唑盐骨架-67-衍生碳三维复合材料(NP CoO x QDs/C).如图2(c)所示，CoO x 量子点提高NP CoO x QDs/C的电导率并缩短Li+的传输路径从而提高了电池的倍率性能.同时，CoO x 量子点被牢牢锚定在碳基材料上，这有利于抑制CoO x 在整个循环过程中的团聚和体积变化，从而提高电池的循环性能.该电极在电流密度为1000 mA/g的条件下循环900次后的比容量仍然有1246 mAh/g.类似地，Wang等[42]通过盐酸多巴胺与Ga2O3的水热反应将Ga2O3量子点成功分散在无定形碳的内部，形成了具有特殊结构的复合物(Ga2O3-QD@NC).碳层的存在可作为Li+快速转移的通道并提供额外的比容量.图2(d)显示出Ga2O3-QD@NC电极的锂化/脱锂过程.在锂化的过程中，Li+通过碳层运输并大量聚集在Ga2O3量子点周围，与量子点反应生成Li x Ga和LiO2.脱锂时，Li+则从量子点周围脱离，Li x Ga分解为Li+和Ga2O3量子点，此时Li+再次穿过碳层向正极移动.这种高度可逆行为使Ga2O3-QD@NC电极表现出优异的电化学性能，其初始放电比容量为1580 mAh/g，首次库仑效率达到62.8%，并且在0.1 A/g条件下循环100次后比容量保持在953 mAh/g，这一性能显著高于其他同类文献.除了碳基材料，其他基体材料也可与金属氧化物量子点复合.Huang等[43]选用笼状硅作为负极基体与低体积膨胀率(<4%)的TiO2量子点复合，有效减少了TiO2量子点的团聚.Si纳米笼具有大量的孔结构，不仅可以促进电解质传输和Li+的扩散，还可以充当电解质的存储结构从而加速电池内的氧化还原反应.同时，具有半开放结构的Si纳米笼也减少了电解质与电极不利的接触面积.这种特殊的结构将会极大提高材料的电化学性能，在1 A/g的电流密度下循环500次仍能保持616.3 mAh/g的高可逆比容量.此外，Fe3O4[44]、MnO[45]、Nb2O5[46]等金属氧化物量子点在碱金属离子电池负极材料中均取得了不错的进展. ...
... Electrochemical properties of quantum dots and their composite materialsTable 1
... 其他的金属氧化物与SnO2和ZnO类似，都存在体积膨胀、电导率低等问题[39-40].缩小氧化物尺寸至量子点级并与基体材料复合能有效解决上述问题.Lu等[41]通过沉淀法制备了CoO x (CoO和Co3O4)量子点和沸石咪唑盐骨架-67-衍生碳三维复合材料(NP CoO x QDs/C).如图2(c)所示，CoO x 量子点提高NP CoO x QDs/C的电导率并缩短Li+的传输路径从而提高了电池的倍率性能.同时，CoO x 量子点被牢牢锚定在碳基材料上，这有利于抑制CoO x 在整个循环过程中的团聚和体积变化，从而提高电池的循环性能.该电极在电流密度为1000 mA/g的条件下循环900次后的比容量仍然有1246 mAh/g.类似地，Wang等[42]通过盐酸多巴胺与Ga2O3的水热反应将Ga2O3量子点成功分散在无定形碳的内部，形成了具有特殊结构的复合物(Ga2O3-QD@NC).碳层的存在可作为Li+快速转移的通道并提供额外的比容量.图2(d)显示出Ga2O3-QD@NC电极的锂化/脱锂过程.在锂化的过程中，Li+通过碳层运输并大量聚集在Ga2O3量子点周围，与量子点反应生成Li x Ga和LiO2.脱锂时，Li+则从量子点周围脱离，Li x Ga分解为Li+和Ga2O3量子点，此时Li+再次穿过碳层向正极移动.这种高度可逆行为使Ga2O3-QD@NC电极表现出优异的电化学性能，其初始放电比容量为1580 mAh/g，首次库仑效率达到62.8%，并且在0.1 A/g条件下循环100次后比容量保持在953 mAh/g，这一性能显著高于其他同类文献.除了碳基材料，其他基体材料也可与金属氧化物量子点复合.Huang等[43]选用笼状硅作为负极基体与低体积膨胀率(<4%)的TiO2量子点复合，有效减少了TiO2量子点的团聚.Si纳米笼具有大量的孔结构，不仅可以促进电解质传输和Li+的扩散，还可以充当电解质的存储结构从而加速电池内的氧化还原反应.同时，具有半开放结构的Si纳米笼也减少了电解质与电极不利的接触面积.这种特殊的结构将会极大提高材料的电化学性能，在1 A/g的电流密度下循环500次仍能保持616.3 mAh/g的高可逆比容量.此外，Fe3O4[44]、MnO[45]、Nb2O5[46]等金属氧化物量子点在碱金属离子电池负极材料中均取得了不错的进展. ...
... Electrochemical properties of quantum dots and their composite materialsTable 1
... 其他的金属氧化物与SnO2和ZnO类似，都存在体积膨胀、电导率低等问题[39-40].缩小氧化物尺寸至量子点级并与基体材料复合能有效解决上述问题.Lu等[41]通过沉淀法制备了CoO x (CoO和Co3O4)量子点和沸石咪唑盐骨架-67-衍生碳三维复合材料(NP CoO x QDs/C).如图2(c)所示，CoO x 量子点提高NP CoO x QDs/C的电导率并缩短Li+的传输路径从而提高了电池的倍率性能.同时，CoO x 量子点被牢牢锚定在碳基材料上，这有利于抑制CoO x 在整个循环过程中的团聚和体积变化，从而提高电池的循环性能.该电极在电流密度为1000 mA/g的条件下循环900次后的比容量仍然有1246 mAh/g.类似地，Wang等[42]通过盐酸多巴胺与Ga2O3的水热反应将Ga2O3量子点成功分散在无定形碳的内部，形成了具有特殊结构的复合物(Ga2O3-QD@NC).碳层的存在可作为Li+快速转移的通道并提供额外的比容量.图2(d)显示出Ga2O3-QD@NC电极的锂化/脱锂过程.在锂化的过程中，Li+通过碳层运输并大量聚集在Ga2O3量子点周围，与量子点反应生成Li x Ga和LiO2.脱锂时，Li+则从量子点周围脱离，Li x Ga分解为Li+和Ga2O3量子点，此时Li+再次穿过碳层向正极移动.这种高度可逆行为使Ga2O3-QD@NC电极表现出优异的电化学性能，其初始放电比容量为1580 mAh/g，首次库仑效率达到62.8%，并且在0.1 A/g条件下循环100次后比容量保持在953 mAh/g，这一性能显著高于其他同类文献.除了碳基材料，其他基体材料也可与金属氧化物量子点复合.Huang等[43]选用笼状硅作为负极基体与低体积膨胀率(<4%)的TiO2量子点复合，有效减少了TiO2量子点的团聚.Si纳米笼具有大量的孔结构，不仅可以促进电解质传输和Li+的扩散，还可以充当电解质的存储结构从而加速电池内的氧化还原反应.同时，具有半开放结构的Si纳米笼也减少了电解质与电极不利的接触面积.这种特殊的结构将会极大提高材料的电化学性能，在1 A/g的电流密度下循环500次仍能保持616.3 mAh/g的高可逆比容量.此外，Fe3O4[44]、MnO[45]、Nb2O5[46]等金属氧化物量子点在碱金属离子电池负极材料中均取得了不错的进展. ...
1
... 其他的金属氧化物与SnO2和ZnO类似，都存在体积膨胀、电导率低等问题[39-40].缩小氧化物尺寸至量子点级并与基体材料复合能有效解决上述问题.Lu等[41]通过沉淀法制备了CoO x (CoO和Co3O4)量子点和沸石咪唑盐骨架-67-衍生碳三维复合材料(NP CoO x QDs/C).如图2(c)所示，CoO x 量子点提高NP CoO x QDs/C的电导率并缩短Li+的传输路径从而提高了电池的倍率性能.同时，CoO x 量子点被牢牢锚定在碳基材料上，这有利于抑制CoO x 在整个循环过程中的团聚和体积变化，从而提高电池的循环性能.该电极在电流密度为1000 mA/g的条件下循环900次后的比容量仍然有1246 mAh/g.类似地，Wang等[42]通过盐酸多巴胺与Ga2O3的水热反应将Ga2O3量子点成功分散在无定形碳的内部，形成了具有特殊结构的复合物(Ga2O3-QD@NC).碳层的存在可作为Li+快速转移的通道并提供额外的比容量.图2(d)显示出Ga2O3-QD@NC电极的锂化/脱锂过程.在锂化的过程中，Li+通过碳层运输并大量聚集在Ga2O3量子点周围，与量子点反应生成Li x Ga和LiO2.脱锂时，Li+则从量子点周围脱离，Li x Ga分解为Li+和Ga2O3量子点，此时Li+再次穿过碳层向正极移动.这种高度可逆行为使Ga2O3-QD@NC电极表现出优异的电化学性能，其初始放电比容量为1580 mAh/g，首次库仑效率达到62.8%，并且在0.1 A/g条件下循环100次后比容量保持在953 mAh/g，这一性能显著高于其他同类文献.除了碳基材料，其他基体材料也可与金属氧化物量子点复合.Huang等[43]选用笼状硅作为负极基体与低体积膨胀率(<4%)的TiO2量子点复合，有效减少了TiO2量子点的团聚.Si纳米笼具有大量的孔结构，不仅可以促进电解质传输和Li+的扩散，还可以充当电解质的存储结构从而加速电池内的氧化还原反应.同时，具有半开放结构的Si纳米笼也减少了电解质与电极不利的接触面积.这种特殊的结构将会极大提高材料的电化学性能，在1 A/g的电流密度下循环500次仍能保持616.3 mAh/g的高可逆比容量.此外，Fe3O4[44]、MnO[45]、Nb2O5[46]等金属氧化物量子点在碱金属离子电池负极材料中均取得了不错的进展. ...
... Fang等[54]受地球通过地质板块运动释放内部应力以保持结构稳定性的启发，提出了一种滑动策略来减小充放电循环过程中体积变化.他们通过溶剂热法将ZnS量子点均匀分散在相互交织重叠的纳米片上，合成了具有分层结构的复合材料[如图3(a)所示，ZnS-QDs@mNC]，该材料可以通过锂化/脱锂过程中的滑动行为有效适应体积变化.如图3(b)所示，在锂化的过程中，ZnS量子点的各向同性膨胀可以有效吸收体积变化的应力，同时碳纳米片的滑移可利用纳米片间的间隙适应ZnS量子点的体积变化，这种滑动行为使ZnS-QDs@mNC负极的体积膨胀仅有6.5%.Shin等[55]通过静电纺丝、硫化和热蒸发成功将1T-WS2量子点嵌入多层中空毛细管束碳纳米纤维.如图3(c)所示，PNCFs上的1T-WS2量子点能够提供丰富的锂存储位点，中空的毛细管束能够缩短Li+的通道，提高Li+的扩散速率，同时由于1T-WS2被固定在PNCFs上，其在锂化和脱锂过程中的体积膨胀得到抑制.从而使该负极材料在充放电过程中表现出较高的比容量(100 mA/g下循环100次后比容量为716.5 mAh/g)、优异的倍率性能和循环稳定性(528.1 mAh/g下循环1000次后容量保持率为87.8%).此外，Guo等[56]利用一步合成法在含N、S掺杂的超薄碳纳米片上原位形成了CoS x 量子点.碳纳米片上富集大量的N和S为钠的存储提供丰富的活性位点和较高电导率，同时超细的CoS x 量子点结构和异质结构提高了CoS x 的稳定性，从而提高了材料的离子和电子导电性.如图3(d)所示，在放电后，电极上的CoS x 量子点转化为Co纳米颗粒并形成SEI层，之后充电过程中Co纳米颗粒会催化SEI层的分解形成CoS x 量子点，这表明该电极是高度可逆的.电极表面形成的可逆SEI层不仅提高了电极初始库仑效率(94.5%)，而且提供了更多的可逆容量(约为658 mAh/g).同时，该电极还表现出优异的倍率性能，如图3(e)所示，即使在10 A/g的高电流密度下，CoS x @NSC-1电极仍然可以保持高于500 mAh/g的可逆比容量，显著高于NSC电极.
(a) Low magnification TEM image of ZnS-QDs@mNC<sup>[<xref ref-type="bibr" rid="R54">54</xref>]</sup>; (b) Schematic illustration of ZnS-QDs@mNC before and after lithiation<sup>[<xref ref-type="bibr" rid="R54">54</xref>]</sup>; (c) Schematic illustration of the three main effects on WS<sub>2</sub>-PCNF10 for boosting ultrafast lithium storage performances<sup>[<xref ref-type="bibr" rid="R55">55</xref>]</sup>; (d) Schematic illustration of the reversible SEI layer formation on the CoS <i><sub>x</sub></i> @NSC-1 electrode<sup>[<xref ref-type="bibr" rid="R56">56</xref>]</sup>; (e) Specific capacities of the NSC and CoS <i><sub>x</sub></i> @NSC-y electrodes at varied current densities<sup>[<xref ref-type="bibr" rid="R56">56</xref>]</sup>Fig. 33 金属氮化物量子点复合物
... Fang等[54]受地球通过地质板块运动释放内部应力以保持结构稳定性的启发，提出了一种滑动策略来减小充放电循环过程中体积变化.他们通过溶剂热法将ZnS量子点均匀分散在相互交织重叠的纳米片上，合成了具有分层结构的复合材料[如图3(a)所示，ZnS-QDs@mNC]，该材料可以通过锂化/脱锂过程中的滑动行为有效适应体积变化.如图3(b)所示，在锂化的过程中，ZnS量子点的各向同性膨胀可以有效吸收体积变化的应力，同时碳纳米片的滑移可利用纳米片间的间隙适应ZnS量子点的体积变化，这种滑动行为使ZnS-QDs@mNC负极的体积膨胀仅有6.5%.Shin等[55]通过静电纺丝、硫化和热蒸发成功将1T-WS2量子点嵌入多层中空毛细管束碳纳米纤维.如图3(c)所示，PNCFs上的1T-WS2量子点能够提供丰富的锂存储位点，中空的毛细管束能够缩短Li+的通道，提高Li+的扩散速率，同时由于1T-WS2被固定在PNCFs上，其在锂化和脱锂过程中的体积膨胀得到抑制.从而使该负极材料在充放电过程中表现出较高的比容量(100 mA/g下循环100次后比容量为716.5 mAh/g)、优异的倍率性能和循环稳定性(528.1 mAh/g下循环1000次后容量保持率为87.8%).此外，Guo等[56]利用一步合成法在含N、S掺杂的超薄碳纳米片上原位形成了CoS x 量子点.碳纳米片上富集大量的N和S为钠的存储提供丰富的活性位点和较高电导率，同时超细的CoS x 量子点结构和异质结构提高了CoS x 的稳定性，从而提高了材料的离子和电子导电性.如图3(d)所示，在放电后，电极上的CoS x 量子点转化为Co纳米颗粒并形成SEI层，之后充电过程中Co纳米颗粒会催化SEI层的分解形成CoS x 量子点，这表明该电极是高度可逆的.电极表面形成的可逆SEI层不仅提高了电极初始库仑效率(94.5%)，而且提供了更多的可逆容量(约为658 mAh/g).同时，该电极还表现出优异的倍率性能，如图3(e)所示，即使在10 A/g的高电流密度下，CoS x @NSC-1电极仍然可以保持高于500 mAh/g的可逆比容量，显著高于NSC电极. ...
... [54]；(b) ZnS-QDs@mNC锂化前后示意图[54]；(c) WS2-PCNF10的储锂机理示意图[52]；(d) CoS x @NSC-1电极上可逆SEI层的形成示意图[55]；(e) NSC和CoS x @NSC-y电极在不同电流密度下的比容量[56](a) Low magnification TEM image of ZnS-QDs@mNC<sup>[<xref ref-type="bibr" rid="R54">54</xref>]</sup>; (b) Schematic illustration of ZnS-QDs@mNC before and after lithiation<sup>[<xref ref-type="bibr" rid="R54">54</xref>]</sup>; (c) Schematic illustration of the three main effects on WS<sub>2</sub>-PCNF10 for boosting ultrafast lithium storage performances<sup>[<xref ref-type="bibr" rid="R55">55</xref>]</sup>; (d) Schematic illustration of the reversible SEI layer formation on the CoS <i><sub>x</sub></i> @NSC-1 electrode<sup>[<xref ref-type="bibr" rid="R56">56</xref>]</sup>; (e) Specific capacities of the NSC and CoS <i><sub>x</sub></i> @NSC-y electrodes at varied current densities<sup>[<xref ref-type="bibr" rid="R56">56</xref>]</sup>Fig. 33 金属氮化物量子点复合物
... [54]；(c) WS2-PCNF10的储锂机理示意图[52]；(d) CoS x @NSC-1电极上可逆SEI层的形成示意图[55]；(e) NSC和CoS x @NSC-y电极在不同电流密度下的比容量[56](a) Low magnification TEM image of ZnS-QDs@mNC<sup>[<xref ref-type="bibr" rid="R54">54</xref>]</sup>; (b) Schematic illustration of ZnS-QDs@mNC before and after lithiation<sup>[<xref ref-type="bibr" rid="R54">54</xref>]</sup>; (c) Schematic illustration of the three main effects on WS<sub>2</sub>-PCNF10 for boosting ultrafast lithium storage performances<sup>[<xref ref-type="bibr" rid="R55">55</xref>]</sup>; (d) Schematic illustration of the reversible SEI layer formation on the CoS <i><sub>x</sub></i> @NSC-1 electrode<sup>[<xref ref-type="bibr" rid="R56">56</xref>]</sup>; (e) Specific capacities of the NSC and CoS <i><sub>x</sub></i> @NSC-y electrodes at varied current densities<sup>[<xref ref-type="bibr" rid="R56">56</xref>]</sup>Fig. 33 金属氮化物量子点复合物
... [54]; (b) Schematic illustration of ZnS-QDs@mNC before and after lithiation[54]; (c) Schematic illustration of the three main effects on WS2-PCNF10 for boosting ultrafast lithium storage performances[55]; (d) Schematic illustration of the reversible SEI layer formation on the CoS x @NSC-1 electrode[56]; (e) Specific capacities of the NSC and CoS x @NSC-y electrodes at varied current densities[56]Fig. 33 金属氮化物量子点复合物
... [54]; (c) Schematic illustration of the three main effects on WS2-PCNF10 for boosting ultrafast lithium storage performances[55]; (d) Schematic illustration of the reversible SEI layer formation on the CoS x @NSC-1 electrode[56]; (e) Specific capacities of the NSC and CoS x @NSC-y electrodes at varied current densities[56]Fig. 33 金属氮化物量子点复合物
... Fang等[54]受地球通过地质板块运动释放内部应力以保持结构稳定性的启发，提出了一种滑动策略来减小充放电循环过程中体积变化.他们通过溶剂热法将ZnS量子点均匀分散在相互交织重叠的纳米片上，合成了具有分层结构的复合材料[如图3(a)所示，ZnS-QDs@mNC]，该材料可以通过锂化/脱锂过程中的滑动行为有效适应体积变化.如图3(b)所示，在锂化的过程中，ZnS量子点的各向同性膨胀可以有效吸收体积变化的应力，同时碳纳米片的滑移可利用纳米片间的间隙适应ZnS量子点的体积变化，这种滑动行为使ZnS-QDs@mNC负极的体积膨胀仅有6.5%.Shin等[55]通过静电纺丝、硫化和热蒸发成功将1T-WS2量子点嵌入多层中空毛细管束碳纳米纤维.如图3(c)所示，PNCFs上的1T-WS2量子点能够提供丰富的锂存储位点，中空的毛细管束能够缩短Li+的通道，提高Li+的扩散速率，同时由于1T-WS2被固定在PNCFs上，其在锂化和脱锂过程中的体积膨胀得到抑制.从而使该负极材料在充放电过程中表现出较高的比容量(100 mA/g下循环100次后比容量为716.5 mAh/g)、优异的倍率性能和循环稳定性(528.1 mAh/g下循环1000次后容量保持率为87.8%).此外，Guo等[56]利用一步合成法在含N、S掺杂的超薄碳纳米片上原位形成了CoS x 量子点.碳纳米片上富集大量的N和S为钠的存储提供丰富的活性位点和较高电导率，同时超细的CoS x 量子点结构和异质结构提高了CoS x 的稳定性，从而提高了材料的离子和电子导电性.如图3(d)所示，在放电后，电极上的CoS x 量子点转化为Co纳米颗粒并形成SEI层，之后充电过程中Co纳米颗粒会催化SEI层的分解形成CoS x 量子点，这表明该电极是高度可逆的.电极表面形成的可逆SEI层不仅提高了电极初始库仑效率(94.5%)，而且提供了更多的可逆容量(约为658 mAh/g).同时，该电极还表现出优异的倍率性能，如图3(e)所示，即使在10 A/g的高电流密度下，CoS x @NSC-1电极仍然可以保持高于500 mAh/g的可逆比容量，显著高于NSC电极. ...
... [55]；(e) NSC和CoS x @NSC-y电极在不同电流密度下的比容量[56](a) Low magnification TEM image of ZnS-QDs@mNC<sup>[<xref ref-type="bibr" rid="R54">54</xref>]</sup>; (b) Schematic illustration of ZnS-QDs@mNC before and after lithiation<sup>[<xref ref-type="bibr" rid="R54">54</xref>]</sup>; (c) Schematic illustration of the three main effects on WS<sub>2</sub>-PCNF10 for boosting ultrafast lithium storage performances<sup>[<xref ref-type="bibr" rid="R55">55</xref>]</sup>; (d) Schematic illustration of the reversible SEI layer formation on the CoS <i><sub>x</sub></i> @NSC-1 electrode<sup>[<xref ref-type="bibr" rid="R56">56</xref>]</sup>; (e) Specific capacities of the NSC and CoS <i><sub>x</sub></i> @NSC-y electrodes at varied current densities<sup>[<xref ref-type="bibr" rid="R56">56</xref>]</sup>Fig. 33 金属氮化物量子点复合物
... [55]; (d) Schematic illustration of the reversible SEI layer formation on the CoS x @NSC-1 electrode[56]; (e) Specific capacities of the NSC and CoS x @NSC-y electrodes at varied current densities[56]Fig. 33 金属氮化物量子点复合物
... Fang等[54]受地球通过地质板块运动释放内部应力以保持结构稳定性的启发，提出了一种滑动策略来减小充放电循环过程中体积变化.他们通过溶剂热法将ZnS量子点均匀分散在相互交织重叠的纳米片上，合成了具有分层结构的复合材料[如图3(a)所示，ZnS-QDs@mNC]，该材料可以通过锂化/脱锂过程中的滑动行为有效适应体积变化.如图3(b)所示，在锂化的过程中，ZnS量子点的各向同性膨胀可以有效吸收体积变化的应力，同时碳纳米片的滑移可利用纳米片间的间隙适应ZnS量子点的体积变化，这种滑动行为使ZnS-QDs@mNC负极的体积膨胀仅有6.5%.Shin等[55]通过静电纺丝、硫化和热蒸发成功将1T-WS2量子点嵌入多层中空毛细管束碳纳米纤维.如图3(c)所示，PNCFs上的1T-WS2量子点能够提供丰富的锂存储位点，中空的毛细管束能够缩短Li+的通道，提高Li+的扩散速率，同时由于1T-WS2被固定在PNCFs上，其在锂化和脱锂过程中的体积膨胀得到抑制.从而使该负极材料在充放电过程中表现出较高的比容量(100 mA/g下循环100次后比容量为716.5 mAh/g)、优异的倍率性能和循环稳定性(528.1 mAh/g下循环1000次后容量保持率为87.8%).此外，Guo等[56]利用一步合成法在含N、S掺杂的超薄碳纳米片上原位形成了CoS x 量子点.碳纳米片上富集大量的N和S为钠的存储提供丰富的活性位点和较高电导率，同时超细的CoS x 量子点结构和异质结构提高了CoS x 的稳定性，从而提高了材料的离子和电子导电性.如图3(d)所示，在放电后，电极上的CoS x 量子点转化为Co纳米颗粒并形成SEI层，之后充电过程中Co纳米颗粒会催化SEI层的分解形成CoS x 量子点，这表明该电极是高度可逆的.电极表面形成的可逆SEI层不仅提高了电极初始库仑效率(94.5%)，而且提供了更多的可逆容量(约为658 mAh/g).同时，该电极还表现出优异的倍率性能，如图3(e)所示，即使在10 A/g的高电流密度下，CoS x @NSC-1电极仍然可以保持高于500 mAh/g的可逆比容量，显著高于NSC电极. ...
... [56](a) Low magnification TEM image of ZnS-QDs@mNC<sup>[<xref ref-type="bibr" rid="R54">54</xref>]</sup>; (b) Schematic illustration of ZnS-QDs@mNC before and after lithiation<sup>[<xref ref-type="bibr" rid="R54">54</xref>]</sup>; (c) Schematic illustration of the three main effects on WS<sub>2</sub>-PCNF10 for boosting ultrafast lithium storage performances<sup>[<xref ref-type="bibr" rid="R55">55</xref>]</sup>; (d) Schematic illustration of the reversible SEI layer formation on the CoS <i><sub>x</sub></i> @NSC-1 electrode<sup>[<xref ref-type="bibr" rid="R56">56</xref>]</sup>; (e) Specific capacities of the NSC and CoS <i><sub>x</sub></i> @NSC-y electrodes at varied current densities<sup>[<xref ref-type="bibr" rid="R56">56</xref>]</sup>Fig. 33 金属氮化物量子点复合物
... [61]；(b) VN-bulk NPs、VN@NC NPs和VNQD@NC HSs的锂化/脱锂示意图[62]；(c) VN-QDS/CM-600在0.5 A/g下的循环性能图[63]；(d)带有NH4VO3 的VNQD的TEM图[64](a) Schematic representation of the Na<sup>+</sup> storage mechanism for TiN/C composite anodes<sup>[<xref ref-type="bibr" rid="R61">61</xref>]</sup>; (b) Schematic illustration of lithiation and delithiation mechanisms for VN-bulk NPs, VN@NC NPs and VNQD@NC HSs<sup>[<xref ref-type="bibr" rid="R62">62</xref>]</sup>; (c) Cycling performance of VN-QDS/CM-600 at 0.5 A/g<sup>[<xref ref-type="bibr" rid="R63">63</xref>]</sup>; (d) TEM images of VNQD with NH<sub>4</sub>VO<sub>3</sub><sup>[<xref ref-type="bibr" rid="R64">64</xref>]</sup>Fig. 4
... [61]; (b) Schematic illustration of lithiation and delithiation mechanisms for VN-bulk NPs, VN@NC NPs and VNQD@NC HSs[62]; (c) Cycling performance of VN-QDS/CM-600 at 0.5 A/g[63]; (d) TEM images of VNQD with NH4VO3[64]Fig. 4
(a) Schematic representation of the Na<sup>+</sup> storage mechanism for TiN/C composite anodes<sup>[<xref ref-type="bibr" rid="R61">61</xref>]</sup>; (b) Schematic illustration of lithiation and delithiation mechanisms for VN-bulk NPs, VN@NC NPs and VNQD@NC HSs<sup>[<xref ref-type="bibr" rid="R62">62</xref>]</sup>; (c) Cycling performance of VN-QDS/CM-600 at 0.5 A/g<sup>[<xref ref-type="bibr" rid="R63">63</xref>]</sup>; (d) TEM images of VNQD with NH<sub>4</sub>VO<sub>3</sub><sup>[<xref ref-type="bibr" rid="R64">64</xref>]</sup>Fig. 4
(a) Schematic representation of the Na<sup>+</sup> storage mechanism for TiN/C composite anodes<sup>[<xref ref-type="bibr" rid="R61">61</xref>]</sup>; (b) Schematic illustration of lithiation and delithiation mechanisms for VN-bulk NPs, VN@NC NPs and VNQD@NC HSs<sup>[<xref ref-type="bibr" rid="R62">62</xref>]</sup>; (c) Cycling performance of VN-QDS/CM-600 at 0.5 A/g<sup>[<xref ref-type="bibr" rid="R63">63</xref>]</sup>; (d) TEM images of VNQD with NH<sub>4</sub>VO<sub>3</sub><sup>[<xref ref-type="bibr" rid="R64">64</xref>]</sup>Fig. 4
(a) Schematic representation of the Na<sup>+</sup> storage mechanism for TiN/C composite anodes<sup>[<xref ref-type="bibr" rid="R61">61</xref>]</sup>; (b) Schematic illustration of lithiation and delithiation mechanisms for VN-bulk NPs, VN@NC NPs and VNQD@NC HSs<sup>[<xref ref-type="bibr" rid="R62">62</xref>]</sup>; (c) Cycling performance of VN-QDS/CM-600 at 0.5 A/g<sup>[<xref ref-type="bibr" rid="R63">63</xref>]</sup>; (d) TEM images of VNQD with NH<sub>4</sub>VO<sub>3</sub><sup>[<xref ref-type="bibr" rid="R64">64</xref>]</sup>Fig. 4
... [67]；(b) 4个Li+ 在C24H12 、2个Li+ 在C24H12 、5个Li+ 在C54H18 、3个Li+ 在C54H18 上的吸附模式[68]；(c) GQDs@CNT的TEM图像[69]；(d) LTO/N-GQD/Super-P分层结构形成示意图[71]；(e) LTO和LTO-NGQ20电极从0.2 C到50 C的倍率性能[71](a) Schematic of the structures of CDs<sup>[<xref ref-type="bibr" rid="R67">67</xref>]</sup>; (b) Adsorption patterns for on four ions on C<sub>24</sub>H<sub>12</sub>, two ions on C<sub>24</sub>H<sub>12</sub>, five ions on C<sub>54</sub>H<sub>18</sub>, three ions on C<sub>54</sub>H<sub>18</sub><sup>[<xref ref-type="bibr" rid="R68">68</xref>]</sup>; (c) TEM images of the GQDs@CNT<sup>[<xref ref-type="bibr" rid="R69">69</xref>]</sup>; (d) Schematic diagrams showing the formation of the hierarchical LTO/N-GQD/Super-P structure<sup>[<xref ref-type="bibr" rid="R71">71</xref>]</sup>; (e) Rate capability of pristine LTO and LTO-NGQ20 electrodes from 0.2 C to 50 C<sup>[<xref ref-type="bibr" rid="R71">71</xref>]</sup>Fig. 5
... [67]; (b) Adsorption patterns for on four ions on C24H12, two ions on C24H12, five ions on C54H18, three ions on C54H18[68]; (c) TEM images of the GQDs@CNT[69]; (d) Schematic diagrams showing the formation of the hierarchical LTO/N-GQD/Super-P structure[71]; (e) Rate capability of pristine LTO and LTO-NGQ20 electrodes from 0.2 C to 50 C[71]Fig. 5
(a) Schematic of the structures of CDs<sup>[<xref ref-type="bibr" rid="R67">67</xref>]</sup>; (b) Adsorption patterns for on four ions on C<sub>24</sub>H<sub>12</sub>, two ions on C<sub>24</sub>H<sub>12</sub>, five ions on C<sub>54</sub>H<sub>18</sub>, three ions on C<sub>54</sub>H<sub>18</sub><sup>[<xref ref-type="bibr" rid="R68">68</xref>]</sup>; (c) TEM images of the GQDs@CNT<sup>[<xref ref-type="bibr" rid="R69">69</xref>]</sup>; (d) Schematic diagrams showing the formation of the hierarchical LTO/N-GQD/Super-P structure<sup>[<xref ref-type="bibr" rid="R71">71</xref>]</sup>; (e) Rate capability of pristine LTO and LTO-NGQ20 electrodes from 0.2 C to 50 C<sup>[<xref ref-type="bibr" rid="R71">71</xref>]</sup>Fig. 5
... [68]; (c) TEM images of the GQDs@CNT[69]; (d) Schematic diagrams showing the formation of the hierarchical LTO/N-GQD/Super-P structure[71]; (e) Rate capability of pristine LTO and LTO-NGQ20 electrodes from 0.2 C to 50 C[71]Fig. 5
(a) Schematic of the structures of CDs<sup>[<xref ref-type="bibr" rid="R67">67</xref>]</sup>; (b) Adsorption patterns for on four ions on C<sub>24</sub>H<sub>12</sub>, two ions on C<sub>24</sub>H<sub>12</sub>, five ions on C<sub>54</sub>H<sub>18</sub>, three ions on C<sub>54</sub>H<sub>18</sub><sup>[<xref ref-type="bibr" rid="R68">68</xref>]</sup>; (c) TEM images of the GQDs@CNT<sup>[<xref ref-type="bibr" rid="R69">69</xref>]</sup>; (d) Schematic diagrams showing the formation of the hierarchical LTO/N-GQD/Super-P structure<sup>[<xref ref-type="bibr" rid="R71">71</xref>]</sup>; (e) Rate capability of pristine LTO and LTO-NGQ20 electrodes from 0.2 C to 50 C<sup>[<xref ref-type="bibr" rid="R71">71</xref>]</sup>Fig. 5
... [69]; (d) Schematic diagrams showing the formation of the hierarchical LTO/N-GQD/Super-P structure[71]; (e) Rate capability of pristine LTO and LTO-NGQ20 electrodes from 0.2 C to 50 C[71]Fig. 5
(a) Schematic of the structures of CDs<sup>[<xref ref-type="bibr" rid="R67">67</xref>]</sup>; (b) Adsorption patterns for on four ions on C<sub>24</sub>H<sub>12</sub>, two ions on C<sub>24</sub>H<sub>12</sub>, five ions on C<sub>54</sub>H<sub>18</sub>, three ions on C<sub>54</sub>H<sub>18</sub><sup>[<xref ref-type="bibr" rid="R68">68</xref>]</sup>; (c) TEM images of the GQDs@CNT<sup>[<xref ref-type="bibr" rid="R69">69</xref>]</sup>; (d) Schematic diagrams showing the formation of the hierarchical LTO/N-GQD/Super-P structure<sup>[<xref ref-type="bibr" rid="R71">71</xref>]</sup>; (e) Rate capability of pristine LTO and LTO-NGQ20 electrodes from 0.2 C to 50 C<sup>[<xref ref-type="bibr" rid="R71">71</xref>]</sup>Fig. 5
... [71](a) Schematic of the structures of CDs<sup>[<xref ref-type="bibr" rid="R67">67</xref>]</sup>; (b) Adsorption patterns for on four ions on C<sub>24</sub>H<sub>12</sub>, two ions on C<sub>24</sub>H<sub>12</sub>, five ions on C<sub>54</sub>H<sub>18</sub>, three ions on C<sub>54</sub>H<sub>18</sub><sup>[<xref ref-type="bibr" rid="R68">68</xref>]</sup>; (c) TEM images of the GQDs@CNT<sup>[<xref ref-type="bibr" rid="R69">69</xref>]</sup>; (d) Schematic diagrams showing the formation of the hierarchical LTO/N-GQD/Super-P structure<sup>[<xref ref-type="bibr" rid="R71">71</xref>]</sup>; (e) Rate capability of pristine LTO and LTO-NGQ20 electrodes from 0.2 C to 50 C<sup>[<xref ref-type="bibr" rid="R71">71</xref>]</sup>Fig. 5
... [73]；(b) CDs@rGO堆叠模型机理图[74]；(c) LAP-rGO-CDs合成示意图[75]；(d) F-CQD@etched-Cu电极提高快速循环性能的3种效应示意图[78](a) Illustration the advantage of surface functional group-tailored BN-CQD structure<sup>[<xref ref-type="bibr" rid="R73">73</xref>]</sup>; (b) Schematic diagram of CDs@rGO stacked models<sup>[<xref ref-type="bibr" rid="R74">74</xref>]</sup>; (c) Schematic of the preparation process for LAP-rGO-CDs<sup>[<xref ref-type="bibr" rid="R75">75</xref>]</sup>; (d) Schematic illustration of the three main effects on the F-CQD@etched-Cu electrode for improving ultrafast cycling<sup>[<xref ref-type="bibr" rid="R78">78</xref>]</sup>Fig. 6
... [73]; (b) Schematic diagram of CDs@rGO stacked models[74]; (c) Schematic of the preparation process for LAP-rGO-CDs[75]; (d) Schematic illustration of the three main effects on the F-CQD@etched-Cu electrode for improving ultrafast cycling[78]Fig. 6
(a) Illustration the advantage of surface functional group-tailored BN-CQD structure<sup>[<xref ref-type="bibr" rid="R73">73</xref>]</sup>; (b) Schematic diagram of CDs@rGO stacked models<sup>[<xref ref-type="bibr" rid="R74">74</xref>]</sup>; (c) Schematic of the preparation process for LAP-rGO-CDs<sup>[<xref ref-type="bibr" rid="R75">75</xref>]</sup>; (d) Schematic illustration of the three main effects on the F-CQD@etched-Cu electrode for improving ultrafast cycling<sup>[<xref ref-type="bibr" rid="R78">78</xref>]</sup>Fig. 6
... [74]; (c) Schematic of the preparation process for LAP-rGO-CDs[75]; (d) Schematic illustration of the three main effects on the F-CQD@etched-Cu electrode for improving ultrafast cycling[78]Fig. 6
(a) Illustration the advantage of surface functional group-tailored BN-CQD structure<sup>[<xref ref-type="bibr" rid="R73">73</xref>]</sup>; (b) Schematic diagram of CDs@rGO stacked models<sup>[<xref ref-type="bibr" rid="R74">74</xref>]</sup>; (c) Schematic of the preparation process for LAP-rGO-CDs<sup>[<xref ref-type="bibr" rid="R75">75</xref>]</sup>; (d) Schematic illustration of the three main effects on the F-CQD@etched-Cu electrode for improving ultrafast cycling<sup>[<xref ref-type="bibr" rid="R78">78</xref>]</sup>Fig. 6
(a) Illustration the advantage of surface functional group-tailored BN-CQD structure<sup>[<xref ref-type="bibr" rid="R73">73</xref>]</sup>; (b) Schematic diagram of CDs@rGO stacked models<sup>[<xref ref-type="bibr" rid="R74">74</xref>]</sup>; (c) Schematic of the preparation process for LAP-rGO-CDs<sup>[<xref ref-type="bibr" rid="R75">75</xref>]</sup>; (d) Schematic illustration of the three main effects on the F-CQD@etched-Cu electrode for improving ultrafast cycling<sup>[<xref ref-type="bibr" rid="R78">78</xref>]</sup>Fig. 6
... [79]；(b) SbQD@C在异质界面处的电荷密度差[80]；(c) B@rGO负极的储锂机制以及横截面叠加模型示意图[84](a) Schematics of the lithiation and subsequent delithiation process of the 3DOP Ge@N-C anode and Ge/N-C anode<sup>[<xref ref-type="bibr" rid="R79">79</xref>]</sup>; (b) The difference charge density of SbQD@C at the heterogeneous interface (e/Å<sup>3</sup>)<sup>[<xref ref-type="bibr" rid="R80">80</xref>]</sup>; (c) Proposed mechanism of the B@rGO anode during the lithium storage process; and schematic diagram of the stacked models at the cross-section<sup>[<xref ref-type="bibr" rid="R84">84</xref>]</sup>Fig. 76 其他类型量子点复合物
... [79]; (b) The difference charge density of SbQD@C at the heterogeneous interface (e/Å3)[80]; (c) Proposed mechanism of the B@rGO anode during the lithium storage process; and schematic diagram of the stacked models at the cross-section[84]Fig. 76 其他类型量子点复合物
... [80]；(c) B@rGO负极的储锂机制以及横截面叠加模型示意图[84](a) Schematics of the lithiation and subsequent delithiation process of the 3DOP Ge@N-C anode and Ge/N-C anode<sup>[<xref ref-type="bibr" rid="R79">79</xref>]</sup>; (b) The difference charge density of SbQD@C at the heterogeneous interface (e/Å<sup>3</sup>)<sup>[<xref ref-type="bibr" rid="R80">80</xref>]</sup>; (c) Proposed mechanism of the B@rGO anode during the lithium storage process; and schematic diagram of the stacked models at the cross-section<sup>[<xref ref-type="bibr" rid="R84">84</xref>]</sup>Fig. 76 其他类型量子点复合物
... [80]; (c) Proposed mechanism of the B@rGO anode during the lithium storage process; and schematic diagram of the stacked models at the cross-section[84]Fig. 76 其他类型量子点复合物
... [84](a) Schematics of the lithiation and subsequent delithiation process of the 3DOP Ge@N-C anode and Ge/N-C anode<sup>[<xref ref-type="bibr" rid="R79">79</xref>]</sup>; (b) The difference charge density of SbQD@C at the heterogeneous interface (e/Å<sup>3</sup>)<sup>[<xref ref-type="bibr" rid="R80">80</xref>]</sup>; (c) Proposed mechanism of the B@rGO anode during the lithium storage process; and schematic diagram of the stacked models at the cross-section<sup>[<xref ref-type="bibr" rid="R84">84</xref>]</sup>Fig. 76 其他类型量子点复合物
... [88]；(b) 0D/2D SnSe@f-Ti3C2 复合材料优异性能的机理示意图[91]；(c) Fe2O3/MoO3@N的Li+ 离子扩散路径示意图[93](a) Schematic illustration of Ni<sub>2</sub>P@NPC building-up process<sup>[<xref ref-type="bibr" rid="R88">88</xref>]</sup>; (b) Schematic illustration of the mechanism of the superior performance of 0D/2D SnSe@f-Ti<sub>3</sub>C<sub>2</sub> composites<sup>[<xref ref-type="bibr" rid="R91">91</xref>]</sup>; (c) Li<sup>+</sup> diffusion path of Fe<sub>2</sub>O<sub>3</sub>/MoO<sub>3</sub>@N<sup>[<xref ref-type="bibr" rid="R93">93</xref>]</sup>Fig. 8
... [88]; (b) Schematic illustration of the mechanism of the superior performance of 0D/2D SnSe@f-Ti3C2 composites[91]; (c) Li+ diffusion path of Fe2O3/MoO3@N[93]Fig. 8
(a) Schematic illustration of Ni<sub>2</sub>P@NPC building-up process<sup>[<xref ref-type="bibr" rid="R88">88</xref>]</sup>; (b) Schematic illustration of the mechanism of the superior performance of 0D/2D SnSe@f-Ti<sub>3</sub>C<sub>2</sub> composites<sup>[<xref ref-type="bibr" rid="R91">91</xref>]</sup>; (c) Li<sup>+</sup> diffusion path of Fe<sub>2</sub>O<sub>3</sub>/MoO<sub>3</sub>@N<sup>[<xref ref-type="bibr" rid="R93">93</xref>]</sup>Fig. 8
(a) Schematic illustration of Ni<sub>2</sub>P@NPC building-up process<sup>[<xref ref-type="bibr" rid="R88">88</xref>]</sup>; (b) Schematic illustration of the mechanism of the superior performance of 0D/2D SnSe@f-Ti<sub>3</sub>C<sub>2</sub> composites<sup>[<xref ref-type="bibr" rid="R91">91</xref>]</sup>; (c) Li<sup>+</sup> diffusion path of Fe<sub>2</sub>O<sub>3</sub>/MoO<sub>3</sub>@N<sup>[<xref ref-type="bibr" rid="R93">93</xref>]</sup>Fig. 8
