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　　劉崗，男，漢族，1981年2月出生，中共黨員、九三學(xué)社社員，工學(xué)博士，研究員，博士生導(dǎo)師。現(xiàn)任中國科學(xué)院金屬研究所所長。

　　2009年7月于中國科學(xué)院金屬研究所，獲得博士學(xué)位，期間：2007年3月至2008年10月作為聯(lián)合培養(yǎng)研究生在澳大利亞昆士蘭大學(xué)開展研究工作。2009年7月加入金屬研究所工作。

　　主要從事清潔能源轉(zhuǎn)化用新材料與器件研究。在Nature, Joule, PNAS, Adv. Mater., J. Am. Chem. Soc., Angew. Chem. Int. Ed., Nat. Commun., Natl. Sci. Rev., Sci. Bull.等期刊上發(fā)表論文190余篇，被SCI引用3.2萬次，連續(xù)（2017-2022年）入選全球高被引學(xué)者，獲授權(quán)專利33件。

　　主持了國家重點研發(fā)計劃項目、973計劃項目課題，國家自然科學(xué)基金委杰出青年科學(xué)基金項目、優(yōu)秀青年科學(xué)基金項目、重點項目以及重點國際合作研究項目等十余項。入選首批國家級人才計劃-青年拔尖人才，入選國家級人才計劃-科技創(chuàng)新領(lǐng)軍人才；獲國家自然科學(xué)獎二等獎（第一完成人）、科學(xué)探索獎（新基石科學(xué)基金會）、中國青年科技獎、中國科學(xué)院青年科學(xué)家獎、全國百篇優(yōu)秀博士學(xué)位論文獎等十余項學(xué)術(shù)獎勵；為英國皇家化學(xué)會會士。

　　兼任中國材料研究學(xué)會青年工作委員會及先進陶瓷分委員會副主任、中國可再生能源學(xué)會光化學(xué)專委會副主任，Wiley出版集團MetalMat、EcoEnergy副主編。

簡歷：

1999.9-2003.7  吉林大學(xué)                  材料物理專業(yè) 學(xué)士
　　2003.9-2009.5  中國科學(xué)院金屬研究所      材料學(xué) 博士
　　2007.3-2008.10 澳大利亞昆士蘭大學(xué)        聯(lián)合培養(yǎng)

　　2009.7-2012.7  中國科學(xué)院金屬研究所    “葛庭燧獎研金”獲得者
　　2012.8-2014.9  中國科學(xué)院金屬研究所      項目研究員
　　2014.10-至今   中國科學(xué)院金屬研究所      研究員

研究領(lǐng)域：

太陽能光催化材料

　　新型太陽能電池

承擔(dān)科研項目情況：

自2009起作為項目（課題）負(fù)責(zé)人承擔(dān)了來自國家自然科學(xué)基金委青年基金、面上項目、優(yōu)秀青年基金以及國際(地區(qū))合作與交流項目，科技部973計劃課題，國家高層次人才特殊支持計劃，中國科學(xué)院知識創(chuàng)新工程重點方向性項目課題、太陽能行動計劃課題以及前沿科學(xué)研究重點計劃項目（拔尖青年科學(xué)家類別），英國皇家學(xué)會-牛頓高級學(xué)者基金等項目多項。同時作為項目骨干參加了國家自然科學(xué)基金委重大項目、重點項目，作為中方合作者參加了國家自然科學(xué)基金委海外及港澳學(xué)者合作研究基金（2+4年期）項目。

重要科研成果：

光催化效率是由光催化材料的光吸收、光生電荷的分離轉(zhuǎn)移及表面催化等三方面的特性協(xié)同決定的，深入理解并有效調(diào)控這些特性能為設(shè)計與構(gòu)建高效太陽能轉(zhuǎn)換用光催化材料提供科學(xué)依據(jù)和關(guān)鍵支撐。以典型半導(dǎo)體光催化材料為研究對象，針對控制光催化材料效率的關(guān)鍵科學(xué)問題開展了深入的系統(tǒng)性研究，在實現(xiàn)寬光譜吸收、提升光生電荷的分離轉(zhuǎn)移能力和晶面調(diào)控催化活性等方面取得了系列進展。

寬光譜吸收

致力于通過引入電子結(jié)構(gòu)修飾劑（異質(zhì)原子或缺陷）來增加寬帶隙半導(dǎo)體材料的可見光吸收，從而更加充分地利用太陽光，特別關(guān)注如何通過控制修飾劑的空間分布來實現(xiàn)光吸收邊的帶對帶紅移。同時探索未知的具有寬譜強可見光吸收的光催化材料，且構(gòu)成元素地殼儲量豐富，拓展寬光譜吸收光催化材料庫。

　　Figure 1  Homogeneous N doping in Cs_0.68Ti_1.83O₄. The left panel: UV-visible absorption spectra of (1) homogeneous N doped Cs_0.68Ti_1.83O₄ and (2) surface N doped TiO₂. The right panel: optical photograph of Cs_0.68Ti_1.83O₄ samples before and after homogeneous N doping. (Band-to-band visible-light photon excitation and photoactivity induced by homogeneous nitrogen doping in layered titanates, Chem Mater 2009, 21, 1266-1274)

　　Figure 2  Homogeneous S doping in g-C₃N₄. The left panel: schematic of two lattice N sites for substitutional S in perfect graphitic carbon nitride. The right panel: a typical time course of hydrogen evolution from water containing 10 vol% triethanolamine scavenger by Pt-deposited g-C₃N₄ (a) and g-C₃N_4-xS_x (b) under λ > 300 and 420 nm. (Unique electronic structure induced high photoreactivity of sulfur-doped graphitic C₃N₄, J Am Chem Soc 2010, 132, 11642-11648)

　　Figure 3  A red anatase TiO₂ with a gradient B/N doping. The left panel: optical photograph of the prepared red TiO₂ sample. The right panel: UV-visible absorption of the white TiO₂ and red TiO₂. (A red anatase TiO₂ photocatalyst for solar energy conversion, Energy Environ Sci 2012, 5, 9603-9610)

　　Figure 4  Homogeneous modification with nitrogen vacancies in g-C₃N₄. The left panel: schematic of the two dimensional sheets of pristine g-C₃N₄ (melon). The right panel: UV-visible absorption spectra of g-C₃N₄ and g-C₃N_4-x (obtained by reducing g-C₃N₄ in a hydrogen atmosphere). (Increasing the visible light absorption of graphitic carbon nitride (melon) photocatalysts by homogeneous self-modification with nitrogen vacancies, Adv Mater 2014, 26, 8046)

Figure 5 Homogeneous amorphization of g-C₃N₄. The left panel: schematic of the two dimensional sheets of disordered pristine g-C₃N₄. The right panel: UV-visible absorption spectra of g-C₃N₄ and amorphous C₃N₄ (obtained by heating g-C₃N₄ in an argon atmosphere). (An amorphous carbon nitride photocatalyst with greatly extended visible-light-responsive range for photocatalytic hydrogen generation, Adv. Mater., 2015, 27, 4572)

Figure 6 α-S photocatalyst. The left panel: UV-visible absorption spectrum of α-sulfur. The inset is a photograph of the α-S crystal powder. The right panel: Applied potential bias dependence of the photocurrent generated by the photoanode of α-S crystals under UV-visible and visible light irradiation. (α-sulfur crystals as a visible light active photocatalyst, J Am Chem Soc 2012, 134, 9070-9073)

Figure 7 β-boron photocatalyst. The left panel: schematic of atomic structure of β-boron. The right panel: UV-visible absorption spectra of boron powder with and without surface amorphous layer (Visible-light-responsive β-rhombohedral boron photocatalysts, Angew Chem Int Ed 2013, 52, 6242-6245)

提升光生電荷的分離轉(zhuǎn)移能力

　　致力于通過降低光催化材料在某一個或兩個方向的尺寸至納米量級，從而縮短光生載流子從體相擴散至表面所經(jīng)歷的路徑，進而降低光生電子空穴的復(fù)合幾率，提高光催化活性；通過選擇性組合具有合適特性的組元來構(gòu)筑具有優(yōu)異空間電荷分離功能的異質(zhì)結(jié)構(gòu)。

　　Figure 8  g-C₃N₄ nanosheets. SEM images of bulk g-C₃N₄ and g-C₃N₄ nanosheets (Graphene-like carbon nitride nanosheets for improved photocatalytic activities, Adv Funct Mater 2012, 22, 4763-4770)

　　Figure 9  Photoanode of Ta₃N₅ nanorod arrays. SEM image of Ta₃N₅ nanorod arrays supported on Ta substrate and photoelectrochemical water oxidation activity of Co(OH)x modified Ta₃N₅ (Template-free synthesis of Ta₃N₅ nanorod arrays for efficient photoelectrochemical water splitting, Chem Commun 2013, 49, 3019-3021)

Figure 10 TEM images of (a) pristine g-C3N4 and (b) porous g-C3N4 photocatalysts after loading Au particles (black particles) via a photodeposition method. The spatial distribution of Au particles on photocatalysts shows the abundance of reductive sites. Scale bars are 50 nm. (Selective breaking of hydrogen bonds of layered carbon nitride towards greatly enhanced visible light photocatalysis, Adv. Mater., 2016, 28, 6471–6477)

　　Figure 11  CdS/ZnS core-shell particles. The left panel: schematic of CdS-mesoporous ZnS core-shell particles with the separation of charge carriers. The middle and right panels: photocatalytic hydrogen generation with ZnS, CdS, and the core-shell particles from the aqueous solution of Na₂S/Na₂SO₃ under visible light. (CdS-mesoporous ZnS core-shell particles for efficient and stable photocatalytic hydrogen evolution under visible light, Energy Environ Sci 2014, 7, 1895–1901)

　　Figure 12  TaB₂/Ta₂O₅ core/shell particles. The left panel: schematic of a TEM image of TaB₂/Ta₂O₅ core/shell particles with a function of promoting the separation of photoexcited electrons and holes. The right panel: band alignment of Ta₂O₅ referring to Fermi level of TaB₂ and Pt as co-catalyst. (Constructing metallic/semiconducting TaB₂/Ta₂O₅ core/shell heterostructure for photocatalytic hydrogen evolution, Adv Energy Mater 2014, 4, 1400057)

Figure 13 Comparison of photocatalytic hydrogen generation from mixture of water/methanol with pristine rutile TiO₂ and Ti³⁺/Ti⁴⁺ core/shell rutile TiO₂ particles after loading 1 wt% Pt co-catalyst. (Enhanced photocatalytic H2 production in core-shell engineered rutile TiO₂, Adv. Mate., 2016, 28, 5850-5856)

晶面調(diào)控催化活性

　　致力于通過控制晶體生長過程中不同晶面的選擇性暴露，實現(xiàn)對光催化材料的表面原子結(jié)構(gòu)的有效調(diào)控，研究表面結(jié)構(gòu)-光催化活性的關(guān)聯(lián)規(guī)律，為基于晶面控制設(shè)計高性能光催化材料打下基礎(chǔ)。

Figure 14  N doped anatase TiO₂ crystal with dominant {001} facets. UV-visible absorption spectrum of nitrogen doped anatase TiO₂ crystals with dominant {001}. The insets are optical photograph and SEM image of nitrogen doped anatase TiO₂ crystals with dominant {001}. (Visible light responsive nitrogen doped anatase TiO₂ sheets with dominant {001} facets derived from TiN, J Am Chem Soc 2009, 131, 12868-12869)

Figure 15  Anatase TiO₂ crystals with a predominance of low index facets. Schematic (A) and SEM images (B-D) of anatase TiO₂ single crystals with different percentages of {001}, {101}, and {010} facets. (On the true photoreactivity order of {001}, {010} and {101} facets of anatase TiO₂ crystals, Angew Chem Int Ed 2011, 50, 2133-2137)

Figure 16  {001} dominated Anatase TiO₂ microspheres with tunable spatial distribution of boron. The left panel: SEM images of anatase TiO₂ microsphere with nearly 100% {001} surface. The right panel: schematic of boron distribution in the microsphere before and after heating. (Heteroatom-modulated switching of photocatalytic hydrogen and oxygen evolution preferences of anatase TiO₂ microspheres, Adv Funct Mater 2012, 22, 3233–3238)

　　Figure 17  Ferroelectric field assisted selective deposition of co-catalysts on different sides of facet. (a) Schematic of single-domain & single crystalline ferroelectric material with in-built electric field; (b) SEM image of PbTiO₃ nanoplates with dominant {001} facets; (c) SEM image of PbTiO₃ nanoplates with a selective depositionof Au and MnOx on different sides; (d) Comparison of photocatalytic hydrogen generation between the PbTiO₃ with the selective deposition of reducing co-catalyst Pt and the PbTiO₃ with the nonselective deposition of reducing co-catalyst Pt. (Selective Deposition of Redox Co-catalysts to Improve the Photocatalytic Activity of Single-Domain Ferroelectric PbTiO₃ Nanoplates, Chemical Communications 2014, 50, 10416 -10419)

Figure 18 Crystal facet dependent interfacial electric conductivity in faceted anatase TiO₂ crystal. I-V curves along different crystallography orientations were measured by contacting one TiO₂ particle with two tungsten probes in SEM microscope. (Greatly enhanced electronic conduction and lithium storage of faceted TiO₂ crystals supported on metallic substrates by tuning crystallographic orientation of TiO₂, Adv. Mater., 2015, 27 3507–3512)