【目的】预测不同气候条件下樟子松Pinus sylvestris var. mongolica在中国的潜在分布及迁移,确定影响樟子松分布的主要环境变量,为樟子松合理引种与保护提供理论依据。【方法】根据200个樟子松分布点和20个环境变量,利用R语言中ENMeva...【目的】预测不同气候条件下樟子松Pinus sylvestris var. mongolica在中国的潜在分布及迁移,确定影响樟子松分布的主要环境变量,为樟子松合理引种与保护提供理论依据。【方法】根据200个樟子松分布点和20个环境变量,利用R语言中ENMeval数据包优化最大熵模型(MaxEnt)并利用ArcGIS空间分析技术对当前气候条件下樟子松在中国潜在分布进行模拟,通过Pearson相关分析和方差膨胀因子分析结合预建模结果对环境因子的筛选,综合Jackknife检验和相关系数,分析樟子松主导限制因子,预测樟子松从当前到未来时期(2050s和2100s)的3种气候情景(SSP126、SSP245和SSP585)下适生区变化趋势。【结果】MaxEnt模型受训者工作特征曲线都大于0.94,说明模型精度较高,能较好预测樟子松潜在分布;影响樟子松分布的主导因子为最冷季度平均气温、降水量季节性变化、最冷月最低气温、温度季节变动系数、最干季度平均气温和最热月最高气温,累计贡献率为92.9%;当前气候条件下,樟子松的适宜分布区主要位于中国大兴安岭地区,总适宜区面积占中国总面积的6.72%;未来时期不同气候条件下樟子松潜在分布区面积减少,质心向西北高纬度和西南降水量充沛地区迁移。【结论】以年为单位的温度和降水是樟子松分布的主要影响因子,当前樟子松的适生区主要在中国大兴安岭地区,未来樟子松分布区有向现有分布区的西北和西南地区迁移的趋势。图1表7参29。展开更多
The effects of annealing treatment on the microstructure and electrochemical properties of low-Co LaNi 3.55 Mn 0.35 Co 0.20 Al 0.20 Cu 0.75 Fe 0.10 hydrogen storage alloys were investigated. X-ray diffraction （XRD） ...The effects of annealing treatment on the microstructure and electrochemical properties of low-Co LaNi 3.55 Mn 0.35 Co 0.20 Al 0.20 Cu 0.75 Fe 0.10 hydrogen storage alloys were investigated. X-ray diffraction （XRD） analysis indicated that annealing treatment remarkably reduced the lattice strain and defects, and increased the unit-cell volume. The optical microscope analysis showed that the as-cast alloy had a crass dendrite microstructure with noticeable composition segregation, which gradually disappeared with increasing annealing temperature, and the micro-structure changed to an equiaxed structure after annealing the alloy at 1233 K. The electrochemical tests indicated that the annealed alloys demonstrated much better cycling stability compared with the as-cast one. The capacity retention at the 100th cycle increased from 90.0% （as-cast） to 94.7% （1273 K）. The annealing treatment also improved the discharge capacity. However, the high rate dischargeability （HRD） value of the annealed alloy slightly dropped, which was believed to be ascribed to the decreased exchange current density and the hydrogen diffusion coefficient in alloy bulk.展开更多
REMg8.35Ni2.18Al0.21 （RE=La, Ce, Pr, and Nd） alloys were prepared by induction melting and following annealing. X-ray diffraction （XRD） and scanning electron microscopy （SEM） results showed that the alloys were ...REMg8.35Ni2.18Al0.21 （RE=La, Ce, Pr, and Nd） alloys were prepared by induction melting and following annealing. X-ray diffraction （XRD） and scanning electron microscopy （SEM） results showed that the alloys were composed of Mg2Ni, （La, Pr, Nd）MgzNi, （La, Ce）2MgxT, （Ce, Pr, Nd）Mg12 and Ce2Ni7 phases. The above phases were disproportioned into Mg2NiH4, MgH2 and REHx （x=2.5 1 or 3） phases in hydriding. CEH2.51 phase transformed into CEH2.29 phase in dehydriding, whereas LaH3, PrH3 and NdH3 phases re- mained unchanged. The PrMg8.41Ni2.14Al0.20 alloy had the fastest hydriding kinetics and the highest dehydriding plateau pressure while the CeMg8.35Ni2.18Al0.21 alloy presented the best hydriding/dehydriding reversibility. The onset hydrogen desorption tempera- ture of the CeMg8.35Ni2.18Al0.21 hydride decreased remarkably owing to the phase transformation between the Cell2.51 and the CEH2.29.展开更多
The phase structure and hydrogen storage properties of LaMg 3.70 Ni 1.18 alloy were investigated. The LaMg 3.70 Ni 1.18 alloy consists of main LaMg 2 Ni phase, minor La 2 Mg 17 and LaMg 3 phases. The alloy can be acti...The phase structure and hydrogen storage properties of LaMg 3.70 Ni 1.18 alloy were investigated. The LaMg 3.70 Ni 1.18 alloy consists of main LaMg 2 Ni phase, minor La 2 Mg 17 and LaMg 3 phases. The alloy can be activated in the first hydriding/dehydriding process, and initial LaMg 2 Ni, La 2 Mg 17 , and LaMg 3 phases transfer to LaH 2.34 , Mg, and Mg 2 Ni phases after activation. The reversible hydrogen storage capacity of the LaMg 3.70 Ni 1.18 alloy is 2.47 wt.% at 558 K, which is higher than that of the LaMg 2 Ni alloy. The pressure-composition-temperature （PCT） curves display two hydriding plateaus, corresponding to the formation of MgH 2 and Mg 2 NiH 4 . However, only one dehydriding plateau is observed, owing to the synergetic effect of hydrogen desorption between MgH 2 and Mg 2 NiH 4 . The uptake time for hydrogen content to reach 99% of saturated state is less than 250 s, and 90% hydrogen can be released in 1200 s in the experimental conditions, showing fast kinetics in hydriding and dehydriding. The activation energies of the LaMg 3.70 Ni 1.18 alloy are –51.5 ± 1.1 kJ/mol and –57.0 ± 0.6 kJ/mol for hydriding and dehydriding, respectively. The hydriding/dehydriding kinetics of the LaMg 3.70 Ni 1.18 alloy is better than that of the Mg 2 Ni alloy, owing to the lower activation energy values.展开更多
文摘【目的】预测不同气候条件下樟子松Pinus sylvestris var. mongolica在中国的潜在分布及迁移,确定影响樟子松分布的主要环境变量,为樟子松合理引种与保护提供理论依据。【方法】根据200个樟子松分布点和20个环境变量,利用R语言中ENMeval数据包优化最大熵模型(MaxEnt)并利用ArcGIS空间分析技术对当前气候条件下樟子松在中国潜在分布进行模拟,通过Pearson相关分析和方差膨胀因子分析结合预建模结果对环境因子的筛选,综合Jackknife检验和相关系数,分析樟子松主导限制因子,预测樟子松从当前到未来时期(2050s和2100s)的3种气候情景(SSP126、SSP245和SSP585)下适生区变化趋势。【结果】MaxEnt模型受训者工作特征曲线都大于0.94,说明模型精度较高,能较好预测樟子松潜在分布;影响樟子松分布的主导因子为最冷季度平均气温、降水量季节性变化、最冷月最低气温、温度季节变动系数、最干季度平均气温和最热月最高气温,累计贡献率为92.9%;当前气候条件下,樟子松的适宜分布区主要位于中国大兴安岭地区,总适宜区面积占中国总面积的6.72%;未来时期不同气候条件下樟子松潜在分布区面积减少,质心向西北高纬度和西南降水量充沛地区迁移。【结论】以年为单位的温度和降水是樟子松分布的主要影响因子,当前樟子松的适生区主要在中国大兴安岭地区,未来樟子松分布区有向现有分布区的西北和西南地区迁移的趋势。图1表7参29。
基金supported by the National Natural Science Foundation of China (No. 20673093)the Natural Science Foundation of Hebei Province, China (No. B2007000303)
文摘The effects of annealing treatment on the microstructure and electrochemical properties of low-Co LaNi 3.55 Mn 0.35 Co 0.20 Al 0.20 Cu 0.75 Fe 0.10 hydrogen storage alloys were investigated. X-ray diffraction （XRD） analysis indicated that annealing treatment remarkably reduced the lattice strain and defects, and increased the unit-cell volume. The optical microscope analysis showed that the as-cast alloy had a crass dendrite microstructure with noticeable composition segregation, which gradually disappeared with increasing annealing temperature, and the micro-structure changed to an equiaxed structure after annealing the alloy at 1233 K. The electrochemical tests indicated that the annealed alloys demonstrated much better cycling stability compared with the as-cast one. The capacity retention at the 100th cycle increased from 90.0% （as-cast） to 94.7% （1273 K）. The annealing treatment also improved the discharge capacity. However, the high rate dischargeability （HRD） value of the annealed alloy slightly dropped, which was believed to be ascribed to the decreased exchange current density and the hydrogen diffusion coefficient in alloy bulk.
基金Foundation item： Project supported by National High-Tech Research and Development Program of China （2007AA05Z 117）, National Natural Science Foundation of China （50971112, 51171165）, China Postdoctoral Science Foundation （20100470990） and Natural Science Founda- tion of Hebei Province （E2010001170）
文摘REMg8.35Ni2.18Al0.21 （RE=La, Ce, Pr, and Nd） alloys were prepared by induction melting and following annealing. X-ray diffraction （XRD） and scanning electron microscopy （SEM） results showed that the alloys were composed of Mg2Ni, （La, Pr, Nd）MgzNi, （La, Ce）2MgxT, （Ce, Pr, Nd）Mg12 and Ce2Ni7 phases. The above phases were disproportioned into Mg2NiH4, MgH2 and REHx （x=2.5 1 or 3） phases in hydriding. CEH2.51 phase transformed into CEH2.29 phase in dehydriding, whereas LaH3, PrH3 and NdH3 phases re- mained unchanged. The PrMg8.41Ni2.14Al0.20 alloy had the fastest hydriding kinetics and the highest dehydriding plateau pressure while the CeMg8.35Ni2.18Al0.21 alloy presented the best hydriding/dehydriding reversibility. The onset hydrogen desorption tempera- ture of the CeMg8.35Ni2.18Al0.21 hydride decreased remarkably owing to the phase transformation between the Cell2.51 and the CEH2.29.
基金supported by the High-Tech Research and Development Program of China (No. 2007AA05Z117)the National Natural Science Foundation of China (Nos. 50971112 and 51001043)+1 种基金the China Post-doctoral Science Foundation Funded Project (20100470990)the Natural Science Foundation of Hebei Province, China (No. E2010001170)
文摘The phase structure and hydrogen storage properties of LaMg 3.70 Ni 1.18 alloy were investigated. The LaMg 3.70 Ni 1.18 alloy consists of main LaMg 2 Ni phase, minor La 2 Mg 17 and LaMg 3 phases. The alloy can be activated in the first hydriding/dehydriding process, and initial LaMg 2 Ni, La 2 Mg 17 , and LaMg 3 phases transfer to LaH 2.34 , Mg, and Mg 2 Ni phases after activation. The reversible hydrogen storage capacity of the LaMg 3.70 Ni 1.18 alloy is 2.47 wt.% at 558 K, which is higher than that of the LaMg 2 Ni alloy. The pressure-composition-temperature （PCT） curves display two hydriding plateaus, corresponding to the formation of MgH 2 and Mg 2 NiH 4 . However, only one dehydriding plateau is observed, owing to the synergetic effect of hydrogen desorption between MgH 2 and Mg 2 NiH 4 . The uptake time for hydrogen content to reach 99% of saturated state is less than 250 s, and 90% hydrogen can be released in 1200 s in the experimental conditions, showing fast kinetics in hydriding and dehydriding. The activation energies of the LaMg 3.70 Ni 1.18 alloy are –51.5 ± 1.1 kJ/mol and –57.0 ± 0.6 kJ/mol for hydriding and dehydriding, respectively. The hydriding/dehydriding kinetics of the LaMg 3.70 Ni 1.18 alloy is better than that of the Mg 2 Ni alloy, owing to the lower activation energy values.
