Nearly three-quarters of the growth in global carbon emissions from the burning of fossil fuels and cement production between 2010 and 2012 occurred in China. Yet estimates of Chinese emissions remain subject to large uncertainty; inventories of China's total fossil fuel carbon emissions in 2008 differ by 0.3 gigatonnes of carbon, or 15 per cent. The primary sources of this uncertainty are conflicting estimates of energy consumption and emission factors, the latter being uncertain because of very few actual measurements representative of the mix of Chinese fuels. Here we re-evaluate China's carbon emissions using updated and harmonized energy consumption and clinker production data and two new and comprehensive sets of measured emission factors for Chinese coal. We find that total energy consumption in China was 10 per cent higher in 2000-2012 than the value reported by China's national statistics, that emission factors for Chinese coal are on average 40 per cent lower than the default values recommended by the Intergovernmental Panel on Climate Change, and that emissions from China's cement production are 45 per cent less than recent estimates. Altogether, our revised estimate of China's CO2 emissions from fossil fuel combustion and cement production is 2.49 gigatonnes of carbon (2 standard deviations = ±7.3 per cent) in 2013, which is 14 per cent lower than the emissions reported by other prominent inventories. Over the full period 2000 to 2013, our revised estimates are 2.9 gigatonnes of carbon less than previous estimates of China's cumulative carbon emissions. Our findings suggest that overestimation of China's emissions in 2000-2013 may be larger than China's estimated total forest sink in 1990-2007 (2.66 gigatonnes of carbon) or China's land carbon sink in 2000-2009 (2.6 gigatonnes of carbon)

commercial LIBs with graphite-based materials as anode cannot meet the above requirements due to the limitation of graphite itself. It shows a low theoretical capacity of 372 mAh g −1 , [2] rapid capacity decay, and possible safety issues during cycling process. Recently, transition metal dichalcogenides (TMDs) have attracted widespread attention in the energy storage fields, especially its application in electrodes of LIBs. As a representative of TMDs, MoS 2 has shown fascinating and superior electrochemical performance due to its unique layered structure. [3,4] MoS 2 always exists in the following three phases: 2H, 1T, and 3R phase according to different coordinations of Mo and S atoms. [5][6][7][8][9] The 2H and 1T phase MoS 2 exhibit notable energy storage and conversion performance due to their characteristic structure and rich physical and chemical properties. 2H-MoS 2 is a semiconducting phase with trigonal prismatic structure. Its high theoretical capacity of 670 mAh g −1 renders it fit to be considered as a promising anode material for LIBs. [10,11] However, two severe issues of 2H-MoS 2 electrode still need to be taken into account: 1) the structure destruction induced by the large volume change during lithium-ions intercalating and deintercalating process; 2) the poor electronic conductivity, arising from a large bandgap of about 1.9 eV. [12,13] To overcome these shortcomings, a large amount of efforts was devoted to modify the electrochemical performance of 2H-MoS 2 . Two general ways are: 1) designing nanostructure materials, such as nanotubes, [14] nanosheets, [15] and nanospheres [16] ; 2) hybridizing 2H-MoS 2 with carbonaceous materials, such as graphene. [17,18] Compared with 2H phase MoS 2 , 1T phase MoS 2 presents a metallic transport behavior and its electric conductivity is approximately 5 orders of magnitudes higher than that in semiconducting 2H-MoS 2 . [19] This contributes to the transfer of electrons and ions in the electrode material. Furthermore, 1T-MoS 2 owns an expanded interlayer spacing of about 1 nm, which is nearly 1.5 times larger than that in 2H-MoS 2 (about 0.65 nm). [20,21] Such an expanded interlayer spacing makes lithium ions embedding and de-embedding much easier. However, the conventional methods to fabricate 1T-MoS 2 require an alkali metal intercalation or exfoliation process, which is unstable, dangerous, complicated, and time-consuming. [22] Preparing 1T phase MoS 2 possesses higher conductivity than the 2H phase, which is a key parameter of electrochemical performance for lithium ion batteries (LIBs). Herein, a 1T-MoS 2 /C hybrid is successfully synthesized through facile hydrothermal method with a proper glucose additive. The synthesized hybrid material is composed of smaller and fewer-layer 1T-MoS 2 nanosheets covered by thin carbon layers with an enlarged interlayer spacing of 0.94 nm. When it is used as an anode material for LIBs, the enlarged interlayer spacing facilitates rapid intercalating and deintercalating of lithium ions and accommodates volume change dur...

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