CN106086491A - A kind of Mg-based composite hydrogen storage material and preparation method thereof - Google Patents
A kind of Mg-based composite hydrogen storage material and preparation method thereof Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/00—Making non-ferrous alloys
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- H01M4/02—Electrodes composed of, or comprising, active material
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- H01M4/38—Selection of substances as active materials, active masses, active liquids of elements or alloys
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- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
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Abstract
The present invention relates to a kind of Mg-based composite hydrogen storage material, described Mg-based composite hydrogen storage material is made up of Mg, Ni, Tm, and Tm is any one or two kinds in Mn, Zr, Nb, Al, Ti, and its chemical composition is represented by Mg2Ni(1‑x)Tmx, 0 ＜ x≤0.3；This Mg-based composite hydrogen storage material is with Mg2Ni is principal phase, at Mg2Ni matrix phase situ grows the intermetallic compound Mg of a kind of cubic structure3TmNi2, the Mg accounting for gross weight 4 6% disperses in the alloy, and in strong alkaline electrolytes, first Mg is corroded and is oxidized to the Mg (OH) of densification2Cover at alloy surface, effectively reduce Mg2The corrosion of Ni.Mg-based composite hydrogen storage material of the present invention has good suction/dehydrogenation and resistance to alkali corrosion performance, have a good application prospect in terms of hydrogen storage device and high power capacity nickel-hydrogen secondary cell, its preparation method technique is simple, and the requirement to equipment is low, is effectively saved Financial cost.
Description
Technical field
The present invention relates to Metallic Functional Materials, especially a kind of Mg-based composite hydrogen storage material and preparation method thereof.
Background technology
Hydrogen bearing alloy as the negative material of Ni-MH battery, be the key determining Ni-MH battery capacity and cycle performance because of
Element.The hydrogen bearing alloy having been commercialized at present is mainly AB5Type lanthanon hydrogen storage alloy is (such as LaNi5) and AB2Type Laves phase hydrogen storage
Alloy is (such as TiMn2), they relatively low hydrogen storage contents (< 3wt.%) it is difficult to meet the requirement of new-energy automobile development.LaNi5Type closes
The actual capacity of gold electrode has reached 330～350 mAh/g, close to its theoretical capacity 372mAh/g, promotes electricity further
Pole capacity is the most extremely difficult.It is considered as that a new generation's high capacity hydrogen storage electrode metal mainly has AB3Type rare earth hydrogen storage alloy, with
RMg2Ni9 (R=La/Y/Ca etc.) are the A of representative2B7Type hydrogen storage alloy, V based solid solution hydrogen bearing alloy, and Mg2Ni alloy, its
In with Mg2The theoretical capacity of Ni and V based solid solution is the highest.But there is the problem that actual reversible capacity is low in V based solid solution.Mg2Ni
As the negative pole of Ni-MH battery, it generates Mg in charging process2NiH4, reversible electrochemical theoretical capacity is up to 1000mAh/g
(corresponding gaseous state hydrogen storage content is 3.6 wt.%)；And Mg2Ni is used as the negative material of Ni-MH battery and has good reactivity
Energy.But, Mg2Ni alloy electrode exists that dynamic performance is poor, hydride (Mg2NiH4) the most stable subject matter；It addition,
Mg in charge and discharge process2Ni alloy is very easy to be oxidized to Mg (OH) in strong basicity electrolytic solution2, fine and close Mg (OH)2
Cover on the surface of alloy electrode, hinder H+Spread to electrode interior, cause the dynamic performance of alloy to be remarkably decreased, and lead
Cause capacity attenuation is too fast.Improve Mg2The approach of Ni base hydrogenous alloy performance mainly has two kinds: one to be to be adjusted by doped alloys element
Whole Mg2Ni alloying component and microstructure；Two is to improve and the preparation technology of optimized alloy, as used fast quenching and carrying out alloy
Suitable heat treatment, improves the cycle performance etc. of alloy electrode.Doped alloys element, it is common that with rare earth element (such as La and
Ce etc., or mischmetal), Al, Ti, V and Ca etc. substitute Mg, substitute Ni with Mn, Fe, Co and Pd etc..
Although said method improves Mg the most to a certain extent2Ni alloy is inhaled and is put dynamic performance and corrosion resistance.But mesh
Front Mg2Ni alloy is used as kinetics and the problem of corrosion-resistant that nickel-hydrogen battery negative pole material exists, and it is basic not obtain
Solve.
Chinese invention patent CN 103855371 B discloses a kind of magnesium-based hydrogen-storage electrode alloy hydride, and chemical formula is
Mg3-x-yMnxNiyHm(0.2≤x≤0.8；0.6 ≤ y ≤ 1.2 ；0.7≤m≤4.4)；This hydride by
Mg2NiH4、MnNi、Mn、MgNi2Or MgH2Several things mutually in any one or a few, and Mg3MnNi2Hn(0.8 ≤ n ≤
3.4) constituting, its sintering process is to be warmed up to 500-600 DEG C of insulation 2-10h under an atmosphere of hydrogen, then cools to 320-
360 DEG C of insulation 1-2h, owing to hydrogen is inflammable and explosive, therefore there is potential safety hazard in the preparation process of this material.
Summary of the invention
Problem to be solved by this invention is the deficiency overcoming prior art to exist, it is provided that a kind of Mg-based composite hydrogen storage material
And preparation method thereof.This material is containing novel Mg3TmNi2(Tm is any one or two kinds in Mn, Zr, Nb, Al, Ti) closes
The Mg-based composite hydrogen storage material of metallographic, improves Mg2Ni alloy hydrogen absorption and desorption dynamic performance, improves material in strong basicity simultaneously
Decay resistance in solution.The present invention uses " ball milling-sintering method " to prepare containing novel Mg3TmNi2(Tm is Mn, Zr,
Any one or two kinds in Nb, Al, Ti) Mg-based composite hydrogen storage material of phase, can be used as the hydrogen storage media of hydrogen storage device and novel
The negative material of high-capacity nickel-hydrogen battery.
In the preparation method of Mg-based composite hydrogen storage material of the present invention, Tm in step (1) (Tm is Mn, Zr, Nb, Al,
Any one or two kinds in Ti) content is less than 10 at.%(atomic number percentage ratios), to ensure active substance in composite
Mg2The content of Ni, thus ensure that composite electrode possesses the capacity that comparison is high.Can pass through on the premise of ensureing high power capacity
The content of regulation Tm, it is achieved novel Mg3TmNi2(Tm is any one or two kinds in Mn, Zr, Nb, Al, Ti) alloy phase content
Controllable adjustment.It addition, this law makes in alloy containing a certain amount of magnesium simple substance (4-6wt.%), its in strong alkaline electrolytes
First it is oxidized to form one layer of fine and close Mg (OH)2Protective layer, enhances the resistance to alkali corrosion of alloy, thus improves alloy electricity
The cyclical stability of pole.
Step (1) uses MgH2As presoma, it is possible to decrease the activity of Mg, thus effectively reduce oxidation, improve alloy
The accuracy of composition.
Step (1) uses MgH2As presoma, it is highly active that it decomposes generation in the sintering reaction of step (4)
Mg, is more beneficial for its ensuing alloying reaction and carries out, and generates target phase.
Step (2) uses ball-milling method mixed by the sample configured, make each constituent element be sufficiently mixed uniformly, it is ensured that step
Suddenly in (4), sintering reaction is smoothed out, and makes the alloying element of interpolation generate intended alloy phase.
By compressing for the mixed powder B obtained by step (2) in step (3), increase the contact interface between each constituent element,
To guarantee that in step (4), sintering reaction is smoothed out, the alloying element of interpolation is made to generate intended alloy phase.
In step (4), the high-purity argon gas protection of logical mobility, can be prevented effectively from alloying element oxidized, particularly reduce Mg
Oxidation；Sinter 5-10 hour in 480 ~ 580 DEG C of temperature ranges, make diffusion reaction fully carry out, the complete alloy of alloying element
Change.
The high-purity Ar gas of logical mobility in step (4), protection sample is not oxidized, discharges powder sample sintering process simultaneously
The hydrogen of middle release.
The Low Temperature Solid-Phase sintering method additionally using this law can be prevented effectively from Mg and the Mn volatilization of tradition smelting process existence and make
Becoming the problem that alloying component is inaccurate, the alloying component using this law to prepare is the most uniform.
Concrete scheme is as follows:
A kind of Mg-based composite hydrogen storage material, described Mg-based composite hydrogen storage material is made up of Mg, Ni, Tm, Tm is Mn, Zr, Nb,
Any one or two kinds in Al, Ti, its chemical composition is represented by Mg2Ni(1-x)Tmx, 0 ＜ x≤0.3；The compound storage of this magnesio
Hydrogen material is with Mg2Ni is principal phase, at Mg2Ni matrix phase situ grows the intermetallic compound Mg of a kind of cubic structure3TmNi2,
The Mg accounting for gross weight 4-6% disperses in the alloy.
A kind of method preparing Mg-based composite hydrogen storage material, comprises the following steps:
(1) MgH2, Ni and Tm according to the proportions sample A of mol ratio 2:1-x:x, and 0 ＜ x≤0.3；Described Tm is
Any one or two kinds in Mn, Zr, Nb, Al, Ti；
(2) the sample A prepared in step (1) is enclosed ball grinder in the glove box of band high-purity argon gas atmosphere, carry out ball milling
Mixed powder, obtains mixed-powder sample B；
(3) the mixed-powder sample B that obtains in step (2) is compressing, obtain just base C；
(4) being sintered in vacuum drying oven tubular type by the first base C obtained in step (3), cooling obtains sample D, by sample D
Mechanical Crushing, obtains powder sample and is described Mg-based composite hydrogen storage material after ball milling.
Further, in described step (2), the speed setting of ball milling is 100-300 rev/min, the set of time of mixed powder
For 3-5 hour.
Further, in described step (4), the temperature of sintering is 480-580 DEG C, and the time is 5-10 hour.
Further, described step (4) leads to the high-purity Ar of mobility as protective gas during sintering processes.
Further, in described step (4), the mode of cooling is for cooling to room temperature with the furnace.
The purposes of described Mg-based composite hydrogen storage material, as hydrogen storage media or the negative material of nickel-hydrogen secondary cell.
Beneficial effect: material of the present invention and preparation method thereof has the following advantages and feature:
(1) preparation method of the present invention, uses MgH2As presoma, effectively reduce the oxidation of Mg, ensured alloy
The accuracy of composition, utilizes it to be decomposed to form fresh Mg in sintering process simultaneously and has higher reactivity, is conducive to
Its alloying forms target phase；
(2) preparation method of the present invention, by adding alloying element Tm, (Tm is any one in Mn, Zr, Nb, Al, Ti
Or two kinds) define a kind of novel Ternary intermetallic compounds Mg3TmNi2, it has good resistance to alkali corrosion performance, and
Be conducive to the diffusion of hydrogen during hydrogen is put in charge migration and suction in charge and discharge process；
(3) Mg that the present invention is generated at magnesium matrix situ by Low Temperature Solid-Phase diffusion reaction2Ni and Mg3TmNi2(Tm be Mn,
Any one or two kinds in Zr, Nb, Al, Ti) alloy is mutually dispersed, a small amount of remaining magnesium oxygen at first in charge and discharge process
Metaplasia becomes Mg (OH)2It is coated on electrode active material Mg2Ni surface, to Mg2Ni serves protective effect；
(4) Mg-based composite hydrogen storage material prepared by the present invention contains novel alloy phase Mg3TmNi2(Tm is Mn, Zr, Nb, Al,
Any one or two kinds in Ti), it is dispersed in composite matrix and improves suction hydrogen discharging rate；In charge and discharge process
Accelerate the transfer of electronics, therefore improve polarization of electrode current potential, effectively reduce the corrosion of electrode；
(5) preparation method technique of the present invention is simple, and the requirement to equipment is low, is effectively saved Financial cost.
Accompanying drawing explanation
Fig. 1 is the process chart that the embodiment of the present invention 1 provides；
Fig. 2 is the Mg of the preparation that the embodiment of the present invention 2 provides2Ni0.7Nb0.3、Mg2Ni0.7Zr0.3And Mg2Ni0.7Mn0.3Sample
XRD spectra；
Fig. 3 is Mg2Ni0.7Mn0.3The dehydrogenation kinetic curve of sample；
Fig. 4 is Mg2Ni0.7Mn0.3Sample calculates the Arrhenius figure of dehydrogenation activation energy；
Fig. 5 is Mg2Ni0.7Mn0.3Alloy carries out the backscattered electron image before charge-discharge test；
Fig. 6 is Mg2Ni0.7Mn0.3Make electrode in the strong alkaline electrolytes of 6mol/L, carry out the alloy of 30 charge and discharge cycles
The backscattered electron image of powder.
Detailed description of the invention
Below in conjunction with embodiment, technical solution of the present invention is further elaborated.Unreceipted concrete technology or bar in embodiment
Part person, according to the technology described by the document in this area or condition or is carried out according to product description.Agents useful for same or instrument
Device unreceipted production firm person, be can by city available from conventional products.
Embodiment 1
Preparing Mg-based composite hydrogen storage material, technological process such as Fig. 1, MgH2, Ni and Mn be according to the ratio of 20:7:3 (mol ratio)
Mixing, uses planetary ball mill, and the speed setting of ball milling is 100 revs/min, carries out mixed powder under high-purity argon gas is protected, mixed
The set of time of powder is 5 hours, obtains mixed powder B；
Utilizing stainless steel mould compressing mixed powder B, pressing pressure is 60-120MPa, obtains just base C；
Base C at the beginning of puts into vacuum tube furnace sintering, and logical high-purity Ar, as protective gas, uses mobility atmosphere so that MgH2Decompose
The hydrogen of release is discharged.Sintering temperature is 500 DEG C, and sintering time is 8 hours.Finally take out sample and by its Mechanical Crushing,
Carrying out ball milling on planetary ball mill, available powder sample (a), chemical composition is Mg2Ni0.7Mn0.3。
Embodiment 2
According to the method in embodiment 1, substituting Mn with Nb and Zr, respectively obtain powder sample (b) and (c), chemical analysis is respectively
For Mg2Ni0.7Nb0.3、Mg2Ni0.7Zr0.3.In concrete preparation method as different from Example 1, when preparing powder sample (b), ball
The speed setting of mill is 200 revs/min, and the set of time of mixed powder is 3 hours；Sintering temperature is 480 DEG C, and sintering time is 10 little
Time.When preparing powder sample (c), the speed setting of ball milling is 300 revs/min, and the set of time of mixed powder is 4 hours；Sintering temperature
Degree is 580 DEG C, and sintering time is 5 hours.
Sample (b) in sample (a) in embodiment 1 and embodiment 2 and (c) are carried out XRD analysis test, and its XRD surveys
Examination analysis result such as Fig. 2.
Figure it is seen that sample after Shao Jie all defines between the metal with face-centred cubic structure (FCC configuration)
Compound phase Mg3MnNi2、Mg3NbNi2And Mg3ZrNi2, respectively as shown in Fig. 2 a, 2b and Fig. 2 c.
Embodiment 3
Mg is prepared according to the method in embodiment 12Ni0.7Nb0.2Mn0.1With Mg2Ni, wherein in concrete preparation method with embodiment 1
Except for the difference that, preparation Mg2Ni0.7Nb0.2Mn0.1Time, MgH2, Ni, Nb and Mn according to 20:7:2:1 (mol ratio) ratio mix,
Preparation Mg2During Ni, MgH2, Ni according to 2:1 (mol ratio) ratio mix.
Prepared by sample (b), (c) and the present embodiment in the sample (a) in embodiment 1, embodiment 2
Mg2Ni0.7Nb0.2Mn0.1、Mg2Ni sample is respectively prepared electrode.Concrete manufacture method is as follows:
(1) weigh 2g powder sample, and mix the high-purity nickel powder of 30wt.% as conductive agent, add appropriate binding agent PTFE,
Achates alms bowl is fully milled uniformly；
(2) by the powder sample even spread of mix homogeneously in (1) to the tow sides of the foam nickel sheet of 1cm × 1cm；
(3) by foam nickel sheet Ni-MH battery dedicated diaphragm parcel coated in (2), then pole piece it is pressed on a hydraulic press,
Pressure applied is 60MPa, and pressurize i.e. made alloy electrode after 1 minute.
To Mg2Ni0.7Nb0.3、Mg2Ni0.7Zr0.3、Mg2Ni0.7Mn0.3、Mg2Ni0.7Nb0.2Mn0.1With Mg2Five kinds of sample systems of Ni
The electrode of standby one-tenth carries out Tafel polarization curve test.Method of testing is as follows:
(1) alloy electrode prepared is immersed in the NaOH solution that concentration is 6mol/L, soaks 24 at ambient temperature little
Time, make the powder sample complete wetting in electrode.
(2) three-electrode system is used to produce CHI760D electrochemistry in Shanghai China in morning alloy electrode good for moistening in (1)
Test on work station.Reference electrode uses saturated calomel electrode, and auxiliary electrode is platinum electrode, and Electrode is alloy to be measured
Electrode.
(3) OCP of electrode, then certain voltage scope near the OCP measured first are measured before test
In, test with the scanning speed of 1mV/s, measure the electrokinetic potential pole in the NaOH solution of 6mol/L under electrode room temperature to be measured
Change curve.
The Tafel polarization curve recorded is fitted obtaining their electrochemical parameters such as table 1 below.
Electrochemical parameters from table 1 is it is obvious that the Mg that compares2For Ni, add the pole of Mn, Nb and Zr alloy
Changing current potential to significantly improve, corrosion current diminishes and impedance increases, and Mg is described2Ni0.7Nb0.3、Mg2Ni0.7Zr0.3、Mg2Ni0.7Mn0.3、
Mg2Ni0.7Nb0.2Mn0.1The decay resistance of prepared electrode is relative to Mg2Electrode prepared by Ni significantly improves.
Embodiment 4
The Mg of Example 1 preparation2Ni0.7Mn0.3Sample carries out dehydrogenation kinetics and the charge-discharge test of different temperatures respectively.Sample
Before product carry out dehydrogenation test, first carry out 4 circulations at 260 DEG C and inhale dehydrogenation, make sample fully activate；The sample activated with
It is the most saturated that the Hydrogen Vapor Pressure of 5MPa inhales hydrogen at different temperatures, then starts dehydrogenation at a temperature of correspondence under vacuum and surveys
Examination.Charge-discharge test is using NiOOH as to electrode, and the electric current density of 100mA/g carries out charge-discharge test, charge and discharge cut-off electricity
Pressure is respectively 1.5 and 0.8 volts.
Wherein, Fig. 3 and Fig. 4 is to choose Mg respectively2Ni0.7Mn0.3Sample carries out inhaling puts different temperatures that hydrogen test obtains
Dehydrogenation kinetic curve and the corresponding Arrhenius figure calculating dehydrogenation activation energy.It has good taking off as seen from Figure 3
Hydrogen performance is concrete, from fig. 4, it can be seen that the dehydrogenation reaction activation energy of material is by Mg2-85kJ/mol the H of Ni alloy2Left and right
Significantly reduce to-63.56 kJ/mol H2, this illustrates Mg2Ni0.7Mn0.3The dehydrogenation reaction of sample is lived and can be reduced, and is easier to take off
Hydrogen reacts.
Fig. 5 is Mg2Ni0.7Mn0.3Sample carries out the backscattered electron image before charge-discharge test, and in figure, arrow indication is novel
Alloy phase Mg3MnNi2, by figure it can be seen that it is to be embedded in Mg and Mg what sintering process situ generated2In Ni matrix.
Fig. 6 is Mg2Ni0.7Mn0.3Sample carries out the backscattered electron image after 30 charge and discharge cycles.Brilliant white granule in figure
It it is new alloy phase Mg3MnNi2, Lycoperdon polymorphum Vitt matrix is Mg2Ni, surface covers one layer of dense Mg (OH)2Passivation layer.The brightest
Aobvious Mg is corroded in strong alkaline electrolytes, and new alloy phase Mg3MnNi2Substantially do not corroded, relatively can be seen compared with Fig. 5
Go out it and maintain preferable initial configuration；Active substance Mg2Ni is also at Mg (OH)2Maintain the most former under the protection of passivation layer
Beginning state, illustrative material possesses preferable decay resistance.
Although above it has been shown and described that embodiments of the invention, it is to be understood that above-described embodiment is example
Property, it is impossible to be interpreted as limitation of the present invention, those of ordinary skill in the art is without departing from the principle of the present invention and objective
In the case of above-described embodiment can be changed within the scope of the invention, revise, replace and modification.
Claims (7)
1. a Mg-based composite hydrogen storage material, it is characterised in that: described Mg-based composite hydrogen storage material is made up of Mg, Ni, Tm,
Tm is any one or two kinds in Mn, Zr, Nb, Al, Ti, and its chemical composition is represented by Mg2Ni(1-x)Tmx, 0 ＜ x≤0.3；
This Mg-based composite hydrogen storage material is with Mg2Ni is principal phase, at Mg2Change between the metal of Ni matrix phase situ a kind of cubic structure of growth
Compound Mg3TmNi2, the Mg accounting for gross weight 4-6% disperses in the alloy.
2. the method for the Mg-based composite hydrogen storage material prepared described in claim 1, it is characterised in that: comprise the following steps:
(1) MgH2, Ni and Tm according to the proportions sample A of mol ratio 2:1-x:x, and 0 ＜ x≤0.3；Described Tm is
Any one or two kinds in Mn, Zr, Nb, Al, Ti；
(2) the sample A prepared in step (1) is enclosed ball grinder in the glove box of band high-purity argon gas atmosphere, carry out ball milling
Mixed powder, obtains mixed-powder sample B；
(3) the mixed-powder sample B that obtains in step (2) is compressing, obtain just base C；
(4) being sintered in vacuum drying oven tubular type by the first base C obtained in step (3), cooling obtains sample D, by sample D
Mechanical Crushing, obtains powder sample and is described Mg-based composite hydrogen storage material after ball milling.
The method preparing Mg-based composite hydrogen storage material the most according to claim 2, it is characterised in that: described step (2)
The speed setting of middle ball milling is 100-300 rev/min, and the set of time of mixed powder is 3-5 hour.
The method preparing Mg-based composite hydrogen storage material the most according to claim 2, it is characterised in that: described step (4)
The temperature of middle sintering is 480-580 DEG C, and the time is 5-10 hour.
The method preparing Mg-based composite hydrogen storage material the most according to claim 2, it is characterised in that: described step (4)
The high-purity Ar of mobility is led to as protective gas during middle sintering processes.
The method preparing Mg-based composite hydrogen storage material the most according to claim 2, it is characterised in that: described step (4)
The mode of middle cooling is for cooling to room temperature with the furnace.
7. the purposes of the Mg-based composite hydrogen storage material described in a claim 1, it is characterised in that: as hydrogen storage media or ni-mh
The negative material of secondary cell.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114164369A (en) * | 2021-12-08 | 2022-03-11 | 河北科技大学 | Mg/Ni/In hydrogen storage material and preparation method thereof |
| CN114438386A (en) * | 2022-03-15 | 2022-05-06 | 北京氢冉新能源科技有限公司 | Magnesium-based hydrogen storage material doped with single metal element and preparation method thereof |
| CN114477082A (en) * | 2021-12-28 | 2022-05-13 | 桂林电子科技大学 | Nano Ni-Nb-O doped magnesium hydride hydrogen storage material and preparation method and application thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1271025A (en) * | 2000-05-31 | 2000-10-25 | 南开大学 | Magnesium-base hydrogen storing alloy material |
| JP2004169102A (en) * | 2002-11-19 | 2004-06-17 | Japan Steel Works Ltd:The | Hydrogen storage alloy, and method of heat treatment for hydrogen storage alloy |
| CN1900337A (en) * | 2006-07-26 | 2007-01-24 | 贵州佑邦科技有限公司 | Quaternary magnesium base hydrogen storage alloy, its producing method and use |
-
2016
- 2016-07-07 CN CN201610531544.XA patent/CN106086491A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1271025A (en) * | 2000-05-31 | 2000-10-25 | 南开大学 | Magnesium-base hydrogen storing alloy material |
| JP2004169102A (en) * | 2002-11-19 | 2004-06-17 | Japan Steel Works Ltd:The | Hydrogen storage alloy, and method of heat treatment for hydrogen storage alloy |
| CN1900337A (en) * | 2006-07-26 | 2007-01-24 | 贵州佑邦科技有限公司 | Quaternary magnesium base hydrogen storage alloy, its producing method and use |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114164369A (en) * | 2021-12-08 | 2022-03-11 | 河北科技大学 | Mg/Ni/In hydrogen storage material and preparation method thereof |
| CN114477082A (en) * | 2021-12-28 | 2022-05-13 | 桂林电子科技大学 | Nano Ni-Nb-O doped magnesium hydride hydrogen storage material and preparation method and application thereof |
| CN114477082B (en) * | 2021-12-28 | 2023-07-21 | 桂林电子科技大学 | Nano Ni-Nb-O doped magnesium hydride hydrogen storage material and preparation method and application thereof |
| CN114438386A (en) * | 2022-03-15 | 2022-05-06 | 北京氢冉新能源科技有限公司 | Magnesium-based hydrogen storage material doped with single metal element and preparation method thereof |
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