Hydrogen storage material, hydrogen storage container, and hydrogen supply apparatus

Abstract

Hydrogen storage materials being inexpensive and having hydrogen absorption (storage) and desorption properties suitable for hydrogen storage are provided. The hydrogen storage materials have alloys with an elemental composition of Formula (1), a hydrogen storage container containing the hydrogen storage material, and a hydrogen supply apparatus including the hydrogen storage container:
La.sub.aCe.sub.bSm.sub.cNi.sub.dM.sub.e (1)
wherein M is Mn or both of Mn and Co, a satisfies 0.60a0.90, b satisfies 0b0.30, c satisfies 0.05c0.25, d satisfies 4.75d5.20, e satisfies 0.05e0.40, a+b+c=1, and d+e satisfies 5.10d+e5.35.

Claims

1. A hydrogen storage material, comprising: an alloy having a composition represented by the following Formula (1),
[Chem. 1]
La.sub.aCe.sub.bSm.sub.cNi.sub.dM.sub.e(1) where M is Mn or both of Mn and Co, a satisfies 0.60a0.90, b satisfies 0b 0.30, c satisfies 0.05c0.25, d satisfies 4.75d5.20, e satisfies 0.05e0.40, a+b+c=1, and d+e satisfies 5.10d+e5.35, and wherein the alloy satisfies a relational expression of ln(P.sub.b1/P.sub.b2)0.43: wherein, P.sub.b1 and P.sub.b2 are equilibrium pressure of absorption for absorption hydrogen pressure-composition isotherm (PCT) curves and that of desorption for desorption PCT curves with 0.8wt % H.sub.2 at 20 C., respectively.

2. The hydrogen storage material according to claim 1, wherein c+e satisfies 0.20c+e0.50 in the alloy.

3. The hydrogen storage material according to claim 1, the alloy satisfying a relational expression of [{ln(P.sub.a1)ln(P.sub.a2)}/0.2]1.40: wherein, P.sub.a1 is desorption pressure at a hydrogen amount of 0.3 wt % and P.sub.a2 is hydrogen desorption pressure at a hydrogen absorption of 0.1 wt % for a hydrogen pressure-composition isotherm of desorption for the alloy at 20 C.

4. A hydrogen storage container containing: the hydrogen storage material according to claim 1.

5. A hydrogen supply apparatus comprising: the hydrogen storage container according to claim 4.

Description

BRIEF DESCRIPTION OF DRAWINGS

(1) FIG. 1 shows hydrogen pressure-composition isotherms (PCT curves) of the alloy powder in Example 1 and the alloy powder in Comparative Example 1, measured at 20 C. The y-axis indicates the hydrogen absorption pressure during hydrogen absorption and the hydrogen desorption pressure during hydrogen desorption.

(2) FIG. 2 shows hydrogen pressure-composition isotherms (PCT curves) of the alloy powder in Example 4 and the alloy powder in Example 12, measured at 20 C. The y-axis indicates the hydrogen absorption pressure during hydrogen absorption and the hydrogen desorption pressure during hydrogen desorption.

DESCRIPTION OF EMBODIMENTS

(3) Hereinafter, the present invention will be described in detail. The hydrogen storage materials of the present invention are materials comprising alloys having elemental composition represented by the following Formula (1). The hydrogen storage materials are preferably materials consisting of the alloys of the present invention. Hereinafter, the alloys having elemental composition represented by Formula (1) may also be referred to as an alloy or alloys of the present invention.
[Chem. 2]
La.sub.aCe.sub.bSm.sub.cNi.sub.dM.sub.e (1)

(4) where, M is Mn or both of Mn and Co, a satisfies 0.60a0.90, b satisfies 0b0.30, c satisfies 0.05c0.25, d satisfies 4.75d5.20, e satisfies 0.05ea+b+c=1, and d+e satisfies 5.10d+e5.35.

(5) In Formula (1), a, b, c, d, and e, represent content of the respective elements by atomic ratio, and detailed description thereof is as follows. Hereinafter, the content ratio may be referred to as a content or an amount.

(6) La is effective in increasing the hydrogen absorption amount of invented alloys, and a, which represents the content of La in Formula (1), satisfies 0.60a0.90. The lower limit of a is preferably 0.65a and more preferably 0.68a, and the upper limit of a is preferably a0.85. In a case of a is smaller than the lower limit, the effect of increasing of the hydrogen absorption amount may not be enough, and in a case of a larger than the upper limit, the equilibrium pressure may be too reduced.

(7) Ce is effective in raising the equilibrium pressure of invented alloys, and b, which represents the content of Ce in Formula (1), satisfies 0b0.30. The lower limit of b is preferably 0<b, and the upper limit of b is preferably b0.25 and more preferably b0.22. In a case of b is larger the upper limit, the hysteresis of the PCT curve may be worsen.

(8) Sm is effective in raising the equilibrium pressure and is also effective in improving of squareness in the PCT curve for invented alloys. c, which represents the content of Sm in Formula (1), satisfies 0.05c0.25. The lower limit of c is preferably 0.07c and more preferably 0.10c, and the upper limit of c is preferably c0.23. In a case of c is smaller than the lower limit, the effect of raising the equilibrium pressure may not be enough and the effect of improvement of squareness in the PCT curve may not be attained, and in a case of c is larger than the upper limit, the hydrogen absorption amount may be reduced. In this regard, the squareness refers to the squareness between plateau region and steep pressure dropping region toward end of desorption for desorption PCT curve, thus, improvement of squareness of materials could be regarded as increasing their effective hydrogen capacity. This squareness in the present application will be used as index in later.

(9) Ni is effective in improving the durability of the hydrogen storage alloys according to the present invention and reducing the hysteresis, and d, which represents the content of Ni in Formula (1), satisfies 4.75d5.20. The lower limit of d is preferably 4.80d, and more preferably 4.85d. In a case of d is smaller than the lower limit, the effect of improving the durability and the effect of reducing the hysteresis may not be enough, and in a case of d is larger than the upper limit, the hydrogen absorption amount may be reduced.

(10) M is Mn alone or combination of Mn and Co, and is effective in reducing hysteresis of the PCT curve of invented alloys. e, which represents the content of M in Formula (1), satisfies 0.05e0.40. The lower limit of e is preferably 0.07e. The upper limit of e is preferably e0.35, and more preferably e0.32. In a case of e is smaller than the lower limit, the effect of reducing hysteresis of the PCT curve may not be enough, and in a case of e is higher than the upper limit, the equilibrium pressure may be too low, and the reaction speed of hydrogen absorption and desorption may worsen.

(11) d+e in Formula (1) represents the sum of the contents of Ni and M. The value of d+e affects the hysteresis of the PCT curve and the hydrogen storage amount of the materials of the present invention, and by adjusting the value of d+e to be within the following range, alloys, which have small hysteresis of the PCT curves while maintaining the sufficient hydrogen storage capacity, can be obtained. d+e satisfies 5.10d+e5.35, and the lower limit of d+e is preferably 5.12d+e.

(12) As described above, both Sm and M in Formula (1) are elements effective in raising the equilibrium pressure during hydrogen absorption or desorption, improving the squareness in the PCT curve, and reducing the hysteresis of the PCT curve of invented alloys. In addition, these effects can be enhanced when both elements are applied simultaneously in Formula (1). In Formula (1), c+e satisfies preferably 0.20c+e0.50 and more preferably 0.20c+e0.45.

(13) The elemental composition of the alloys of the present invention can be confirmed by quantitative analysis using an Inductively Coupled Plasma (ICP) analysis apparatus. In the present specification, unless specified, otherwise, the alloys of the present invention refer to the alloys having the elemental composition in accordance with Formula (1).

(14) The alloys of the present invention may contain inevitable impurities derived from raw materials and the like. Examples of the inevitable impurities include, but are not limited to, Pr, Nd, and Al. The acceptable amount of inevitable impurities in the alloys of the present invention is 0.5 mass % or less.

(15) The alloys of the present invention can be obtained as alloy flakes or other shapes as described later. The average grain size of crystal in the alloy flake or slab is preferably 25 to 250 m and more preferably 40 to 230 m. The average grain size of crystal can be measured as follows. The alloy flake or slab was embedded in a normal temperature curable-type resin (for example, an epoxy resin), the resin was cured, embedded alloy was subjected to being cut and precision polishing using a wet polishing machine, and finally the polished cross-section with mirror-like surface was obtained. Next, for example, the cross section of the alloy is etched with a 0.1M nitric acid aqueous solution, then a polarization microscope is used to measure the lengths of the major axial diameter and the minor axial diameter of each grain, and the grain size of the crystal is defined as (length of the major axial diameter+length of the minor axial diameter)/2. The grain size is measured in this way, and the average of three grain size per alloy flake or slab is taken as the average grain size. The size of the alloy flake or slab for measuring the crystal grain size is not particularly limited. For example, an alloy slab of about 1 cm.sup.3 may be used. Further, the grain size may be measured by using an alloy flake of about 1 cm.sup.2, and in that case, the average grain size is preferably 25 to 250 m.

(16) Invented alloys fulfill following equation [{ln(P.sub.a1)ln(P.sub.a2)}/0.2]1.40 in which, P.sub.a1 and P.sub.a2 are equilibrium pressure at 0.3 wt % H.sub.2 and 0.1 wt % H.sub.2 obtained from desorption PCT curve at 20 C., respectively. The materials fulfilling the above expression possess good squareness for desorption PCT curve and their effective hydrogen storage capacities are increased, thus these materials are preferable for hydrogen storage. The results obtained from above expression are regard as the index of squareness of PCT curves for hydrogen desorption. In order to obtain more precise P.sub.a2, it is preferable to measure the hydrogen desorption pressure for several points between 0.08 wt % to 0.12 wt %.

(17) It is preferable that, invented alloys fulfill following equation [{ln(P.sub.a3)ln(P.sub.a1)}/0.8]0.35, and more preferable that [{ln(P.sub.a3)ln(P.sub.a1)}/0.8]0.28 in which, P.sub.a1 and P.sub.a3 are equilibrium pressure at 0.3wt % H.sub.2 and 1.1 wt % H.sub.2 for desorption PCT curve at 20 C., respectively. The materials fulfilling the above expression possess good hydrogen desorption capability such as during hydrogen desorption, equilibrium pressure is well maintained and almost all of absorbed hydrogen corresponding to plateau region could be desorbed from alloys and utilized in related (connected) apparatus and so on. In addition, the relationship of the above expression is used as the index of plateau flatness for hydrogen desorption curves.

(18) Further, it is preferable that, invented alloys fulfill following equation ln(P.sub.b1/P.sub.b2)0.43, in which, Pb.sub.1 and Pb.sub.2 are equilibrium pressure of absorption for absorption PCT curves and that of desorption for desorption PCT curves with 0.8wt % H.sub.2 at 20 C., respectively. The materials with hysteresis of PCT curves fulfilling the above expression possess small hysteresis, which means the materials require moderate hydrogen pressure for hydrogen storage and/or require moderate heat for hydrogen desorption which could improve total running efficiency of storage system by using the invented hydrogen storage materials. Of course, above expression of hysteresis of the PCT could be used as index for evaluation.

(19) Further, preferable hydrogen desorption pressure P.sub.b2 of the invented alloys at a hydrogen absorption amount of 0.8 wt % at 20 C. is 0.05 MPa or higher, and more preferably 0.07 MPa or higher. Such alloys possess good hydrogen desorption properties between room temperature and 95 C. Though there is no particular upper limit in P.sub.b2, so, for example, P.sub.b2 is adjusted about 1.00 MPa at 20 C.

(20) It is particularly preferable that the invented alloys which form the invented hydrogen storage materials fulfill the above-mentioned relationships related with PCT curves, also, the invented alloys which partially do not satisfy mentioned relationships are acceptable.

(21) Next, a method for producing the hydrogen storage materials of the present invention will be described. First, examples of the method for preparing the alloys include strip casting methods such as a single roll method, a twin roll method and a disk method, and a permanent mold casting method.

(22) For example, in the strip casting method, raw materials blended so that the casted alloy will has a desired composition are prepared. The blended raw materials are then melted by heating in an inert gas atmosphere such as Ar to obtain a molten alloy, the molten alloy reached adequate temperature, then the molten alloy is poured on a water-cooled copper roll, rapidly cooled and solidified, thereby alloy flakes are obtained. In the case of permanent mold casting method, a molten alloy is obtained in the same manner as mentioned above, in this method, the molten alloy is poured into a water-cooled copper (or iron) mold, and molten alloys are cooled, solidified and then an ingot or slab is obtained. Usually cooling rate of the strip casting method is much higher than that of the permanent mold casting method, so the strip casting method is generally more preferable than mold casting in order to obtaining alloy flakes with less segregation and uniform element distribution. Depression of segregation and uniformity of elemental distribution are very important for the invented alloys which form the invented hydrogen storage materials, therefore the strip casting method is a preferred method in the present invention as alloy production method.

(23) Note that, in the case of strip casting methods, the preferrable cooling rate of the molten alloy for producing the alloy flakes, is as follows. The cooling rate of molten alloy between liquidus temperature of the molten alloys and 1000 C. is set to be 300 C./sec or higher. The cooling rate is preferably 700 C./sec or higher, more preferably 1000 C./sec or higher, and particularly preferably 4000 C./sec or higher. Though there is no particular upper limit for the cooling rate, the upper limit is practically about 20000 C./sec or lower. Liquidus temperature of the molten alloys are usually within about 1300 to 1500 C., though the temperature varies strongly depending on the alloys' composition.

(24) The cooling rate below 1000 C. is not particularly limited, and for example, in a case of the strip casting method, after being detached from the roll, the alloy flakes may be collected at a temperature of, for example, 100 C. or lower by being cooled.

(25) Furthermore, in order to obtain alloys having a more uniform composition distribution, it is preferable that the alloy flakes obtained by the cooling is subjected to a heat treatment. The heat treatment can be performed within a range of 700 C. or higher and 1200 C. or lower in an inert gas atmosphere such as Ar. The heat treatment temperature is preferably 950 C. or higher and 1150 C. or lower, and the heat treatment time is 1 hour or more and less than 24 hours and preferably 3 hours or more and less than 15 hours.

(26) Next, the alloy flakes obtained by the casting is ground in order to obtain alloy powder. The grinding can be performed by using a known grinder. Average particle size of the alloy powder is preferably 800 m or smaller and more preferably 500 m or smaller. Though it is not necessary to specifically define the smaller limit of the particle size of the alloy powder, the smaller limit is practically about 0.1 m. Here, the particle size of the alloy powder refers to a diameter measured by a sieve shaker (Ro-Tap).

(27) The hydrogen storage materials of the present invention may be such alloy powder, a composite obtained by mixing the alloy powder with a resin or the like and molding the mixture into an arbitrary form such as a granular form, or articles attached on temperature-controllable apparatus. In this case, the resin functions as a binder for the alloy powder. The mixing can be performed by a known method. For example, the mixing can be performed using a mortar, or using a rotary mixer such as a double cone rotary mixer or a V-type rotary mixer, a stirring mixer such as a blade-type stirring mixer or a screw-type stirring mixer, or the like. It is also possible to perform the mixing while grinding the alloy flakes and the binder using a grinder such as a ball mill or an attritor mill.

(28) Hydrogen storage containers of the present invention contain the hydrogen storage materials disclosed above, and as for the materials and shapes of the containers, known materials and a known shape can be used.

(29) A hydrogen supply apparatus of the present invention includes the hydrogen storage container, and as for the configurations other than the container with the invented hydrogen storage materials, known configurations can be used.

EXAMPLES

(30) Hereinafter, the present invention will be described in detail with examples of this invention and Comparative Examples as reference, but the present invention is not limited thereto. In the descriptions of Examples, the alloys of the present invention in Examples and the alloys in Comparative Examples (Comparative examples are the alloys not included the present invention) are all referred to as an alloy or alloys. In addition, an alloy obtained in shape of flakes by the strip casting method is referred to as alloy flakes, and a product obtained by grinding the alloy flakes is referred to as alloy powder.

Example 1

(31) Raw materials were weighed so that finally obtained alloys had the elemental composition shown in Table 1 and melted in a high frequency melting furnace in an argon gas (Ar) atmosphere, thereby molten alloy was prepared. The molten alloy was rapidly cooled and solidified by using a strip casting method, molten alloy was poured at molten temperature of around 1500 C. on a water-cooled copper roll in strip-cast apparatus, and alloy flakes with an average thickness of about 0.3 mm were obtained. Liquidus temperature of the molten alloy was around 1450 C. and the cooling rate during casting between liquidus temperature and 1000 C. was between 6000 C./sec and 9000 C./sec.

(32) The alloy flakes obtained above were subjected to a heat treatment by being kept it in an Ar atmosphere at 1030 C. for 10 hrs by using a heat treatment furnace. For cross-section observation, the heat-treated alloy flakes were embedded in an epoxy resin, the resin was cured and subjected to being cut and precision polishing using a wet polishing machine, and an alloy with mirror-like cross sections was prepared. Then the cross section of the alloy was etched with a 0.1M nitric acid aqueous solution. The average grain size of crystal in the alloy was obtained by using a polarization microscope (manufactured by Olympus Corporation) with the above-described method. In this alloy, the average grain size was 110 m.

(33) After the heat treatment, the heat-treated alloy flakes were also ground by using a stainless-steel mortar, and then alloy powder with particle size of under 500 m was obtained using a sieve having opening size of 500 m.

(34) PCT curves of the alloy powder were obtained by using an automatic high pressure Sieverts apparatus for PCT measurement (manufactured by Fuse Technonet Co., LTD.). The alloy powder was inserted the measurement tube and the tube was connected to Sieverts apparatus, then the measurement tube was placed in oil bath and kept targeted temperature. The measurement tube with alloy powder was vacuumed at 80 C. under around 2.5 Pa (for example 0.5 to 2.5 Pa) for lhr and then initial activation was conducted with following procedure. Hydrogen was provided measurement tube at 0 C. and hydrogenation of alloy powder (hydrogen absorption) taking place, hydrogen pressure was increased up to 2.5 MPa. After saturated with 2.5 MPa of hydrogen, hydrogen was removed (hydrogen desorption) at 80 C. for 0.5 hr (under around 2.5 Pa), then alloy powder was saturated with 2.5 MPa of hydrogen again, this hydrogen desorption/absorption cycle was conducted 2 times as initial activation and then vacuumed 80 C. for 2 hrs (under around 2.5 Pa). The hydrogen absorption and desorption equilibrium pressures of ally powder was measured between 0.01 MPa and 2.0 MPa at 20 C. The obtained hydrogen pressure-composition isotherms (PCT curves) are shown in FIG. 1.

(35) Hydrogen content of alloy powder for hydrogen absorption with 1.0 MPa of H.sub.2, and hydrogen desorption pressure at 0.8 wt % H.sub.2 were obtained from absorption PCT curve and desorption PCT curve, respectively. Results are summarized in Table 1.

(36) The squareness of the PCT curve of hydrogen desorption for the alloy powder was calculated by using equation {ln(P.sub.a1)ln(P.sub.a2)}/0.2 where P.sub.a1 is desorption pressure at 0.3 wt % H.sub.2 and P.sub.a2 at 0.1wt % H.sub.2, respectively, obtained from PCT curve. The results are summarized in Table 1.

(37) The plateau flatness in the PCT curve of hydrogen desorption for the alloy powder was calculated by using equation {ln(P.sub.a3)ln(P.sub.a1)}/0.8 where P.sub.a1 is desorption pressure at 0.3 wt % H.sub.2 and P.sub.a3 at 1.1wt % H.sub.2, respectively obtained from PCT curve. The results are summarized in Table 1.

(38) The hysteresis of the PCT curves for the alloy powder was calculated by using equation In (Pbi/Pb2) where Pbi is absorption pressure at 0.8 wt % H.sub.2 for absorption curve, and P.sub.b2 is desorption pressure at 0.8 wt % H.sub.2 for desorption curve, respectively, obtained from PCT curves. The results are summarized in Table 1.

Examples 2 to 11 and 13

(39) Alloy flakes and alloy powder of each Example were prepared in the same manner as in Example 1 with different chemical composition shown in Table 1, and the hydrogen absorption and desorption properties (squareness and the like) were measured. During alloys preparation pouring temperatures, liquidus temperatures of molten alloys and cooling rates of molten alloys of these Examples between liquidus temperature and 1000 C. were 1500 C., around 1450 C., and between 6000 C./sec and 9000 C./sec, respectively, all of which were approximately the same as those in Example 1. The results are summarized in Table 1. The hydrogen pressure-composition isotherms (PCT curves) of Example 4 are shown in FIG. 2. The average grain sizes of Examples 2, 4 and 6 were 96 m, 85 m, and 105 m, respectively.

Example 12

(40) Alloy was prepared by using mold cast method. Raw materials were weighed and melted by using a high frequency furnace under argon (Ar) atmosphere and then molten alloy was casted at 1500 C. into an iron mold (permanent mold casting), thickness of obtained alloy (slab) was about 25 mm. Chemical composition of Example 12 is summarized in Table 1. Then, alloy was crushed into powder and hydrogen absorption and desorption properties along with squareness of desorption PCT curve, the flatness of plateau and so on were obtained. PCT curves for Example12 were shown in FIG. 2 and other results were summarized in Table 1. In this case (mold casting), liquidus temperature and cooling rate of molten between liquidus temperature and 1000 C. were around 1450 C. and 5 C./sec, respectively, and averaged grain size was around 749 m.

Comparative Examples 1 to 4

(41) Alloy flakes and alloy powder of each Comparative Example were prepared in the same manner as in Example 1 with different elemental composition shown in Table 1, and their hydrogen absorption and desorption properties along with squareness of desorption PCT curves, the flatness of plateau and so on were obtained. The hydrogen pressure-composition isotherms (PCT curves) of Comparative Example 1 are shown in FIG. 1. and obtained results for Comparative Example 1 through 4 are summarized in Table 1. Pouring temperatures, liquidus temperatures, and cooling rates of molten alloys between liquidus temperature and 1000 C. of these Comparative Examples were 1500 C., 1450 C., and between 6000 C./sec and 9000 C./sec, respectively, which were approximately the same as those in Example 1.

(42) TABLE-US-00001 TABLE 1 Hydrogen Hydrogen absorption desorption amount pressure Composition (atomic ratio) (wt %) at (Mpa) at Plateau a(La) b(Ce) c(Sm) d(Ni) e(Mn) e(Co) Al d + e 1.0 Mpa 0.8 wt % Squareness flatness Hysteresis Example 1 0.77 0.05 0.18 5.12 0.14 5.26 1.43 0.32 0.95 0.10 0.32 Example 2 0.77 0.10 0.13 5.07 0.14 0.05 5.26 1.45 0.33 0.85 0.11 0.39 Example 3 0.75 0.12 0.13 5.04 0.14 0.08 5.26 1.44 0.37 0.78 0.11 0.37 Example 4 0.69 0.18 0.13 4.96 0.20 0.10 5.26 1.43 0.34 0.90 0.11 0.36 Example 5 0.75 0.12 0.13 5.02 0.14 0.10 5.26 1.43 0.36 0.72 0.10 0.35 Example 6 0.77 0.10 0.13 5.12 0.14 5.26 1.44 0.33 0.58 0.13 0.43 Example 7 0.77 0.05 0.18 5.16 0.10 5.26 1.41 0.42 0.61 0.12 0.32 Example 8 0.77 0.03 0.20 5.16 0.10 5.26 1.41 0.39 0.71 0.14 0.30 Example 9 0.77 0.23 5.16 0.05 5.21 1.40 0.41 0.61 0.26 0.27 Example 10 0.77 0.23 5.11 0.05 5.16 1.41 0.36 0.51 0.22 0.29 Example 11 0.79 0.06 0.15 5.16 0.10 5.26 1.42 0.38 0.95 0.10 0.36 Example 12 0.69 0.18 0.13 4.96 0.20 0.10 5.26 1.42 0.36 1.08 0.32 0.36 Example 13 0.80 0.02 0.18 4.96 0.30 5.26 1.46 0.11 0.30 0.10 0.42 Comparative 0.87 0.13 5.00 0.15 0.20 5.35 1.44 0.26 1.83 0.13 0.42 Example 1 Comparative 0.73 0.27 4.85 0.30 0.20 5.35 1.38 0.38 4.24 0.16 0.20 Example 2 Comparative 0.64 0.36 4.42 0.18 0.50 5.10 1.47 0.38 2.55 0.14 0.24 Example 3 Comparative 0.74 0.13 0.13 4.88 0.14 0.10 0.14 5.12 1.41 0.18 2.71 0.12 0.15 Example 4

(43) From Table 1, the alloy of each Example has more favorable squareness for PCT curves than those of Comparative Examples which means increasing effective hydrogen desorption capacity of Examples. Each Example absorb hydrogen at normal temperature (for example, at room temperature under moderate hydrogen pressure) and absorbed hydrogen is almost fully desorbed with preferable desorption pressure under room temperature to 95 C. In this invention, hydrogen storage materials with small hysteresis in PCT curves are presented. In addition, invented materials use less amount of cobalt which contribute security of raw (relatively) precious material and reduce materials cost.