LAUSR

p λ p s w s i l Lithium ion batteries (LIBs) have been widely used in portable and smart devices because of their high energy densities, long cycle life and environmental friendliness. In order to meet the evergrowing demand for human-beings utilizing electronic devices, electric vehicles and energy storage grids, it requires LIBs with much higher power and energy densities [1] . As a core of LIBs, the electrode (including cathode and anode) materials largely determine the development of LIBs. Over the past decades, a large number of anode candidates have been developed to replace graphite, the most commonly used commercial anode, with the limited theoretical capacity (372 mAh g −1 ) and poor rate capability. Among the candidates, graphene and its analogues (e.g., graphene derivatives and their related composites) have attracted great attention owing to their overwhelming physical properties of large surface areas, high electrical conductivities, excellent mechanical flexibilities, as well as chemical stabilities [2] . Despite the high theoretical capacity and promising electrochemical performances reported, the charge/mass-transfer capability of graphene based materials as anodes for LIBs remains challenges [3] . One of the great challenges is the strong van der Waals interactions between graphene nanosheets leading to the easy restack and agglomeration during the electrode preparation and discharge-charge process. It is well known that the charge/mass-transfer prefers to reach the edges of graphene and then diffuse along its basal plane (in-plane diffusion) rather than that in through-plane diffusion. On account of this feature, very recently, the holey graphene has attracted a great concern [4–7] . The creation of the throughplane pores within graphene not only enables the electrolyte and charge/mass quickly transporting through holes to reach active sites, but also provides abundant edges along the holes for additional charge/mass loading [8–10] and carbon-edge engineering (e.g., heteroatoms doping [11 , 12] and molecular adsorption [13] ). Benefiting from rich holes as well as the decreased van der Waals interaction, the holey graphene is more prone to forming a thinner and restack film compared to the pristine graphene. As expected, the enlarged accessible surface area and shortened charge/mass diffusion distance endow the holey graphene film with superior power and energy densities, in particular volumetric energy densities [11 , 14] . So far, many effort s have been devoted to fabricating holey graphene by means of various physical (e.g., templateassisted lithography [15] , photodegradation [16] , ion irradiation [17] , plasma etching [18] , chemical vapor deposition [19 , 20] , and hydrothermal methods [14 , 21] ) and chemical approaches (e.g., H 2 O 2 , HNO 3 , H 2 SO 4 and KMnO 4 ) [6 , 7] . However, the former approaches usually suffer from tedious and complex experimental procedures as well as the low yields. The latter one often requires