The La-Mg-Ni-based A2B7-type Lao.8_xNdx Mgo.2Ni3.35Alo.lSio.o5 （x = 0, 0.1, 0.2, 0.3, and 0.4） electrode alloys were prepared by casting and annealing. The influence of the partial substitution of Nd for La on the s...The La-Mg-Ni-based A2B7-type Lao.8_xNdx Mgo.2Ni3.35Alo.lSio.o5 （x = 0, 0.1, 0.2, 0.3, and 0.4） electrode alloys were prepared by casting and annealing. The influence of the partial substitution of Nd for La on the structure and electrochemical performances of the alloys was investigated. The structural analysis of X-ray diffraction and scanning electron microscopy reveals that the experimental alloys consist of two major phases： （La,Mg）2Ni7 with the hexagonal Ce2Ni7-type structure and LaNi5 with the hexagonal CaCus-type structure as well as some residual phases of LaNi3 and NdNis. The electrochemical measurements indicate that an evident change of the electrochemical performance of the alloys is associated with the substitution of Nd for La. The discharge capacity of the alloy first increases then decreases with the growing Nd content, whereas their cycle stability clearly grows all the time. Furthermore, the measurements of the high rate discharge ability, the limiting current density, and hydrogen diffusion coefficient all demonstrate that the electrochemical kinetic properties of the alloy electrodes first augment then decline with the rising amount of Nd substitution.展开更多
The partial substitution of Zr for La has been performed in order to ameliorate the electrochemical hydrogen storage performances of La–Mg–Ni based A2B7-type electrode alloys. The melt spinning technology was used t...The partial substitution of Zr for La has been performed in order to ameliorate the electrochemical hydrogen storage performances of La–Mg–Ni based A2B7-type electrode alloys. The melt spinning technology was used to prepare the La0.75-xZrxMg0.25Ni3.2Co0.2Al0.1 (x=0, 0.05, 0.1, 0.15, 0.2) electrode alloys. The impacts of the melt spinning and the substituting La with Zr on the structures and the electrochemical hydrogen storage characteristics of the alloys were systemically investigated. The analysis of XRD and TEM reveals that the as-cast and spun alloys have a multiphase structure, composing of two main phases (La, Mg)2Ni7 and LaNi5 as well as a residual phase LaNi2. The electrochemical measurement indicates that both the substitution of Zr for La and the melt spinning ameliorate the electrochemical cycle stability of the alloys dramatically. Furthermore, the high rate discharge ability (HRD) of the as-spun (10 m/s) alloys notably declines with growing the amount of Zr substitution, while it first augments and then falls for the (x=0.1) alloy with rising the spinning rate.展开更多
In this paper, we comprehensively investigate the influences of M（M=Cu, Co, Mn） substitution for Ni on the structures and electrochemical hydrogen storage characteristics of the nanocrystalline and amorphous Mg20Ni1...In this paper, we comprehensively investigate the influences of M（M=Cu, Co, Mn） substitution for Ni on the structures and electrochemical hydrogen storage characteristics of the nanocrystalline and amorphous Mg20Ni10-xMx（M=Cu, Co, Mn; x = 0–4） alloys prepared by melt spinning. The as-spun（M=None, Cu） alloys display an entire nanocrystalline structure, whereas the as-spun（M=Co, Mn） alloys hold a mixed structure of both nanocrystalline and amorphous when x = 4（M content）. These results indicate that the substitution of M（M=Co, Mn） for Ni facilitates the glass formation in Mg2Ni-type alloy. All the as-spun alloys have the Mg2 Ni major phase, but M（M=Co, Mn） substitution brings on some secondary phases,such as Mg Co2, Mg phases for M=Co, and Mn Ni, Mg phases for M=Mn. The substitution of M（M=Cu, Co, Mn）for Ni also makes a positive contribution to the cycle stability of the alloys in the following orders：（M=Cu） [（M=Co） [（M=Mn） for x = 1 and（M=Co） [（M=Mn）[（M=Cu） for x = 2–4. Meanwhile, it notably enhances the discharge capacity of the alloys in the sequence of（M=Co） [（M=Mn） [（M=Cu）. As for the high rate discharge ability, it visibly upgrades with the growing of M content for（M=Cu, Co）, while it grows at first and then declines for（M=Mn）.展开更多
The RE-Mg-Ni-Mn-based AB2-type La（1-x）CexMgNi（3.5）Mn（0.5）（ x = 0- 0. 4） alloys were prepared by spinning treatment. For obtaining the optimum performance,the effects of Ce content and spinning rate on the hydr...The RE-Mg-Ni-Mn-based AB2-type La（1-x）CexMgNi（3.5）Mn（0.5）（ x = 0- 0. 4） alloys were prepared by spinning treatment. For obtaining the optimum performance,the effects of Ce content and spinning rate on the hydrogen storage performance of the alloys were studied systematically. The results show that the variations of the spinning rate and Ce content result in noteworthy changes of the phase content without altering phase composition of the alloys. Specifically,the LaMgNi4 phase increases and LaNi5 phase decreases when increasing the spinning rate and Ce content. Furthermore,the crystalline grains of Cecontaining alloys prepared by spinning treatment are remarkably refined. The alloys own superior electrochemical performance. All alloys reach the optimal discharge capacity at the initial cycle. Increasing Ce content and spinning rate lead the discharge capacity and electrochemical kinetics rise to an optimal value and then start to reduce. Meanwhile,the electrochemical cycle stability is also improved,which is ascribed to the great enhancement of anti-pulverization and anti-corrosion abilities resulting from the spinning treatment and the substitution of Ce for La.展开更多
To improve the hydrogen storage performance of PrMg12-type alloys, Ni was adopted to replace partially Mg in the alloys. The PrMgllNi＋x wt.% Ni （x=100, 200） alloys were prepared via mechanical milling. The phase st...To improve the hydrogen storage performance of PrMg12-type alloys, Ni was adopted to replace partially Mg in the alloys. The PrMgllNi＋x wt.% Ni （x=100, 200） alloys were prepared via mechanical milling. The phase structures and morphology of the experimental alloys were in vestigated by X-ray diffraction and transmission electron microscopy. The results show that increasing milling time and Ni content accelerate the formation of nanocrystalline and amorphous structure. The gaseous hydrogen storage properties of the experimental alloys were determined by differential scanning calorimetry （DSC） and Sievert apparatus. In addition, increasing milling time makes the hydrogenation rates of the alloys augment firstly and decline subsequently and the dehydrogenation rate always increases. The maximum capacity is 5. 572 wt. % for the x = 100 alloy and 5. 829 wt. % for the x = 200 alloy, respectively. The enthalpy change （ △H ）, entropy change （△S） and the dehydrogenation activation energy （Exde） markedly lower with increasing the milling time and the Ni content due to the generation of nanocrystalline and amorphous structure.展开更多
To investigate the influence of adding CeO2 on the hydrogen storage characteristics of Sm-Mg-Ni-based SmMg11Ni-type alloy,mechanical milling was utilized to synthesize SrnMg11Ni and SmMg11Ni +5 wt.%CeO2 (named SmMg11N...To investigate the influence of adding CeO2 on the hydrogen storage characteristics of Sm-Mg-Ni-based SmMg11Ni-type alloy,mechanical milling was utilized to synthesize SrnMg11Ni and SmMg11Ni +5 wt.%CeO2 (named SmMg11Ni- 5CeO2)alloys.The microstructure of as-castand as-milled samples was measured via X-ray diffractometer and transmission electron microscope.Sieverts device was utilized to measure the isothermal hydriding and dehydriding kinetics. The non-isothermal dehydrogenation performance was explored by thermogravimetry and differential scanning calorimetry.The hydrogen desorption activation energy of the compound metal hydride can be computed by both Arrhenius and Kissinger methods.The related data show that adding CeO2 can engender a very slight influence on the hydrogen storage thermodynamics,but it can result in an obvious reduction in hydrogen absorption and desorption capacities.Furthermore,the hydrogen desorption performance of experimental alloys is conspicuously ameliorated by the addition of CeO2,viz.lowering the initial hydrogen desorption temperature and enhancing hydrogen desorption rate.The hydrogen desorpfion activation energies with and without CeO2 addition are 84.28 and 100.31 kJ/mol,respectively,with an obvious decrease of 16.03 kJ/mol.This is thought to be responsible for the ameliorated hydrogen desorption kinetics by adding CeO2.展开更多
基金Projects(51761032,51471054)supported by the National Natural Science Foundation of ChinaProject(2015MS0558)supported by the Natural Science Foundation of Inner Mongolia,China
基金supported by the National Natural Science Foundation of China(Nos.51161015 and 50961009)the National High Technology Research and Development Program of China(No.2011AA03A408)the Natural Science Foundation of Inner Mongolia(Nos.2011ZD10 and 2010ZD05)
文摘The La-Mg-Ni-based A2B7-type Lao.8_xNdx Mgo.2Ni3.35Alo.lSio.o5 （x = 0, 0.1, 0.2, 0.3, and 0.4） electrode alloys were prepared by casting and annealing. The influence of the partial substitution of Nd for La on the structure and electrochemical performances of the alloys was investigated. The structural analysis of X-ray diffraction and scanning electron microscopy reveals that the experimental alloys consist of two major phases： （La,Mg）2Ni7 with the hexagonal Ce2Ni7-type structure and LaNi5 with the hexagonal CaCus-type structure as well as some residual phases of LaNi3 and NdNis. The electrochemical measurements indicate that an evident change of the electrochemical performance of the alloys is associated with the substitution of Nd for La. The discharge capacity of the alloy first increases then decreases with the growing Nd content, whereas their cycle stability clearly grows all the time. Furthermore, the measurements of the high rate discharge ability, the limiting current density, and hydrogen diffusion coefficient all demonstrate that the electrochemical kinetic properties of the alloy electrodes first augment then decline with the rising amount of Nd substitution.
文摘The partial substitution of Zr for La has been performed in order to ameliorate the electrochemical hydrogen storage performances of La–Mg–Ni based A2B7-type electrode alloys. The melt spinning technology was used to prepare the La0.75-xZrxMg0.25Ni3.2Co0.2Al0.1 (x=0, 0.05, 0.1, 0.15, 0.2) electrode alloys. The impacts of the melt spinning and the substituting La with Zr on the structures and the electrochemical hydrogen storage characteristics of the alloys were systemically investigated. The analysis of XRD and TEM reveals that the as-cast and spun alloys have a multiphase structure, composing of two main phases (La, Mg)2Ni7 and LaNi5 as well as a residual phase LaNi2. The electrochemical measurement indicates that both the substitution of Zr for La and the melt spinning ameliorate the electrochemical cycle stability of the alloys dramatically. Furthermore, the high rate discharge ability (HRD) of the as-spun (10 m/s) alloys notably declines with growing the amount of Zr substitution, while it first augments and then falls for the (x=0.1) alloy with rising the spinning rate.
基金financially supported by the National Natural Science Foundations of China (No. 51161015)the Natural Science Foundation of Inner Mongolia, China (Nos. 2011ZD10 and 2010ZD05)
文摘In this paper, we comprehensively investigate the influences of M（M=Cu, Co, Mn） substitution for Ni on the structures and electrochemical hydrogen storage characteristics of the nanocrystalline and amorphous Mg20Ni10-xMx（M=Cu, Co, Mn; x = 0–4） alloys prepared by melt spinning. The as-spun（M=None, Cu） alloys display an entire nanocrystalline structure, whereas the as-spun（M=Co, Mn） alloys hold a mixed structure of both nanocrystalline and amorphous when x = 4（M content）. These results indicate that the substitution of M（M=Co, Mn） for Ni facilitates the glass formation in Mg2Ni-type alloy. All the as-spun alloys have the Mg2 Ni major phase, but M（M=Co, Mn） substitution brings on some secondary phases,such as Mg Co2, Mg phases for M=Co, and Mn Ni, Mg phases for M=Mn. The substitution of M（M=Cu, Co, Mn）for Ni also makes a positive contribution to the cycle stability of the alloys in the following orders：（M=Cu） [（M=Co） [（M=Mn） for x = 1 and（M=Co） [（M=Mn）[（M=Cu） for x = 2–4. Meanwhile, it notably enhances the discharge capacity of the alloys in the sequence of（M=Co） [（M=Mn） [（M=Cu）. As for the high rate discharge ability, it visibly upgrades with the growing of M content for（M=Cu, Co）, while it grows at first and then declines for（M=Mn）.
基金financially sponsored by National Natural Science Foundation of China(51371094 and 51471054)
文摘The RE-Mg-Ni-Mn-based AB2-type La（1-x）CexMgNi（3.5）Mn（0.5）（ x = 0- 0. 4） alloys were prepared by spinning treatment. For obtaining the optimum performance,the effects of Ce content and spinning rate on the hydrogen storage performance of the alloys were studied systematically. The results show that the variations of the spinning rate and Ce content result in noteworthy changes of the phase content without altering phase composition of the alloys. Specifically,the LaMgNi4 phase increases and LaNi5 phase decreases when increasing the spinning rate and Ce content. Furthermore,the crystalline grains of Cecontaining alloys prepared by spinning treatment are remarkably refined. The alloys own superior electrochemical performance. All alloys reach the optimal discharge capacity at the initial cycle. Increasing Ce content and spinning rate lead the discharge capacity and electrochemical kinetics rise to an optimal value and then start to reduce. Meanwhile,the electrochemical cycle stability is also improved,which is ascribed to the great enhancement of anti-pulverization and anti-corrosion abilities resulting from the spinning treatment and the substitution of Ce for La.
基金financially sponsored by National Natural Science Foundation of China (51471054)
文摘To improve the hydrogen storage performance of PrMg12-type alloys, Ni was adopted to replace partially Mg in the alloys. The PrMgllNi＋x wt.% Ni （x=100, 200） alloys were prepared via mechanical milling. The phase structures and morphology of the experimental alloys were in vestigated by X-ray diffraction and transmission electron microscopy. The results show that increasing milling time and Ni content accelerate the formation of nanocrystalline and amorphous structure. The gaseous hydrogen storage properties of the experimental alloys were determined by differential scanning calorimetry （DSC） and Sievert apparatus. In addition, increasing milling time makes the hydrogenation rates of the alloys augment firstly and decline subsequently and the dehydrogenation rate always increases. The maximum capacity is 5. 572 wt. % for the x = 100 alloy and 5. 829 wt. % for the x = 200 alloy, respectively. The enthalpy change （ △H ）, entropy change （△S） and the dehydrogenation activation energy （Exde） markedly lower with increasing the milling time and the Ni content due to the generation of nanocrystalline and amorphous structure.
基金the National Natural Science Foundation of China (Grant Nos.51761032, 51471054 and 51871125).
文摘To investigate the influence of adding CeO2 on the hydrogen storage characteristics of Sm-Mg-Ni-based SmMg11Ni-type alloy,mechanical milling was utilized to synthesize SrnMg11Ni and SmMg11Ni +5 wt.%CeO2 (named SmMg11Ni- 5CeO2)alloys.The microstructure of as-castand as-milled samples was measured via X-ray diffractometer and transmission electron microscope.Sieverts device was utilized to measure the isothermal hydriding and dehydriding kinetics. The non-isothermal dehydrogenation performance was explored by thermogravimetry and differential scanning calorimetry.The hydrogen desorption activation energy of the compound metal hydride can be computed by both Arrhenius and Kissinger methods.The related data show that adding CeO2 can engender a very slight influence on the hydrogen storage thermodynamics,but it can result in an obvious reduction in hydrogen absorption and desorption capacities.Furthermore,the hydrogen desorption performance of experimental alloys is conspicuously ameliorated by the addition of CeO2,viz.lowering the initial hydrogen desorption temperature and enhancing hydrogen desorption rate.The hydrogen desorpfion activation energies with and without CeO2 addition are 84.28 and 100.31 kJ/mol,respectively,with an obvious decrease of 16.03 kJ/mol.This is thought to be responsible for the ameliorated hydrogen desorption kinetics by adding CeO2.
