WO2022050268A1 - 水素貯蔵材料、水素貯蔵容器及び水素供給装置 - Google Patents
水素貯蔵材料、水素貯蔵容器及び水素供給装置 Download PDFInfo
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- 239000001257 hydrogen Substances 0.000 title claims abstract description 167
- 229910052739 hydrogen Inorganic materials 0.000 title claims abstract description 167
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 title claims abstract description 161
- 238000003860 storage Methods 0.000 title claims abstract description 73
- 239000011232 storage material Substances 0.000 title claims abstract description 30
- 239000000956 alloy Substances 0.000 claims abstract description 110
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 110
- 239000000203 mixture Substances 0.000 claims abstract description 37
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 10
- 238000010586 diagram Methods 0.000 claims description 11
- 150000002431 hydrogen Chemical class 0.000 abstract description 5
- 238000010521 absorption reaction Methods 0.000 abstract 1
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- 239000002245 particle Substances 0.000 description 13
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 11
- 239000013078 crystal Substances 0.000 description 10
- 229910052751 metal Inorganic materials 0.000 description 10
- 239000002184 metal Substances 0.000 description 10
- 230000000052 comparative effect Effects 0.000 description 8
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- 238000005259 measurement Methods 0.000 description 5
- 229910052718 tin Inorganic materials 0.000 description 5
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 4
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 4
- 229910052804 chromium Inorganic materials 0.000 description 4
- 229910052802 copper Inorganic materials 0.000 description 4
- 239000010949 copper Substances 0.000 description 4
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- 229910052684 Cerium Inorganic materials 0.000 description 1
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- NHNBFGGVMKEFGY-UHFFFAOYSA-N Nitrate Chemical compound [O-][N+]([O-])=O NHNBFGGVMKEFGY-UHFFFAOYSA-N 0.000 description 1
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 1
- 229910010340 TiFe Inorganic materials 0.000 description 1
- 230000004913 activation Effects 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
- C01B3/00—Hydrogen; Gaseous mixtures containing hydrogen; Separation of hydrogen from mixtures containing it; Purification of hydrogen
- C01B3/0005—Reversible uptake of hydrogen by an appropriate medium, i.e. based on physical or chemical sorption phenomena or on reversible chemical reactions, e.g. for hydrogen storage purposes ; Reversible gettering of hydrogen; Reversible uptake of hydrogen by electrodes
- C01B3/001—Reversible uptake of hydrogen by an appropriate medium, i.e. based on physical or chemical sorption phenomena or on reversible chemical reactions, e.g. for hydrogen storage purposes ; Reversible gettering of hydrogen; Reversible uptake of hydrogen by electrodes characterised by the uptaking medium; Treatment thereof
- C01B3/0031—Intermetallic compounds; Metal alloys; Treatment thereof
- C01B3/0047—Intermetallic compounds; Metal alloys; Treatment thereof containing a rare earth metal; Treatment thereof
- C01B3/0057—Intermetallic compounds; Metal alloys; Treatment thereof containing a rare earth metal; Treatment thereof also containing nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/06—Metallic powder characterised by the shape of the particles
- B22F1/068—Flake-like particles
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
- B22F1/14—Treatment of metallic powder
- B22F1/142—Thermal or thermo-mechanical treatment
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/007—Alloys based on nickel or cobalt with a light metal (alkali metal Li, Na, K, Rb, Cs; earth alkali metal Be, Mg, Ca, Sr, Ba, Al Ga, Ge, Ti) or B, Si, Zr, Hf, Sc, Y, lanthanides, actinides, as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2301/00—Metallic composition of the powder or its coating
- B22F2301/15—Nickel or cobalt
- B22F2301/155—Rare Earth - Co or -Ni intermetallic alloys
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C2202/00—Physical properties
- C22C2202/04—Hydrogen absorbing
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/30—Hydrogen technology
- Y02E60/32—Hydrogen storage
Definitions
- the present invention relates to a hydrogen storage material, a hydrogen storage container, and a hydrogen supply device.
- a hydrogen storage alloy is an alloy that can reversibly store and release hydrogen, and has already been used as a negative electrode material for nickel-hydrogen secondary batteries.
- hydrogen has been attracting attention as an energy source. It is also expected to be a material that can safely store hydrogen, and research is continuing on its use in hydrogen storage and supply systems.
- There are various types of hydrogen storage alloys such as AB5 series, AB2 series, TiFe series, and BCC series such as TiVCr. Among them, AB5 series alloys are easy to activate initially, and the plateau of the hydrogen pressure-composition isotherm diagram (PCT curve). Since it has relatively good properties, it is being studied for practical use as a hydrogen storage material.
- the properties required for hydrogen storage materials are easy initial activation, large hydrogen storage capacity, reversible and fast hydrogen storage and release reaction, and practical temperature range (normal temperature to 95 ° C). ), The hydrogen storage / release is performed well, the hysteresis of the hydrogen storage pressure and the hydrogen release pressure is small, the plateau property is good, the cost is low, etc., but in order to meet these demands, the AB5 system As a study of alloys, attempts have been made to add various elements to LaNi 5 .
- LmNi a-x AyB z ( Lm in the formula is La40-70%, Ce0.1-20% and other rare earth metals containing metals such as Nd, Pr, Sm; A is Al, One kind of metal selected from the group of Mn and Fe; B is one kind of metal selected from the group of Mn (except when A is Mn), Co, Zr and V; a is 4.8 ⁇ a ⁇ 5.
- a and B are different metals; C is one of Al and Sn; a, b, c and d are one of Al or Sn represented by 0.01 to 1.0 and Co.
- Disclosed are hydrogen storage materials characterized by their inclusion. Further, it is disclosed that by adding Co and Al or Sn together with one or two kinds of Mn, Fe and Cr to the R—Ni based alloy, the occlusion amount is large and the hysteresis is reduced.
- Patent Document 1 attempts to reduce hysteresis by using an additive element, it uses a relatively large amount of expensive Co, and there remains a problem in terms of hydrogen storage / release rate and cost.
- an object of the present invention is to provide a hydrogen storage material which is inexpensive and has hydrogen storage (storage) release characteristics suitable for hydrogen storage.
- a hydrogen storage material having a large amount of hydrogen storage (storage) and release of hydrogen, capable of storing and releasing hydrogen in a temperature range of room temperature to 95 ° C., and having a small hysteresis of the PCT curve.
- a hydrogen storage container provided with a hydrogen storage material having hydrogen storage and release characteristics suitable for hydrogen storage at low cost, and a hydrogen supply device including the hydrogen storage container.
- an alloy having a composition containing a specific rare earth element and a transition metal element based on LaNi 5 has a small hysteresis and a PCT curve. Has been found to be able to release hydrogen with a large amount of hydrogen that can be released and almost no pressure fluctuation until the end of the release, and has completed the present invention.
- a hydrogen storage material having an alloy having an elemental composition represented by the following formula (1) is provided.
- M is Mn or both Mn and Co.
- a is 0.60 ⁇ a ⁇ 0.90
- b is 0 ⁇ b ⁇ 0.30
- c is 0.05 ⁇ c ⁇ 0.25
- d is 4.75 ⁇ d ⁇ 5.20
- e is 0. 05 ⁇ e ⁇ 0.40
- a + b + c 1, and d + e is 5.10 ⁇ d + e ⁇ 5.35.
- a hydrogen storage container provided with the hydrogen storage material and a hydrogen supply device including the hydrogen storage container are provided.
- the hydrogen storage material of the present invention has an alloy having the above-mentioned specific elemental composition, it has excellent hydrogen storage and release characteristics and can be suitably used for hydrogen storage.
- 6 is a hydrogen pressure-composition isotherm (PCT curve) of the alloy powder of Example 1 and the alloy powder of Comparative Example 1 at 20 ° C.
- the equilibrium pressure on the y-axis indicates the hydrogen storage pressure at the time of hydrogen storage and the hydrogen release pressure at the time of hydrogen release.
- 6 is a hydrogen pressure-composition isotherm (PCT curve) of the alloy powder of Example 4 and the alloy powder of Example 12 at 20 ° C.
- the equilibrium pressure on the y-axis indicates the hydrogen storage pressure at the time of hydrogen storage and the hydrogen release pressure at the time of hydrogen release.
- the hydrogen storage material of the present invention is a material having an alloy having an elemental composition represented by the following formula (1).
- a material made of the alloy is preferable.
- the alloy having an elemental composition represented by the formula (1) may be referred to as an alloy of the present invention.
- M is Mn or both Mn and Co.
- a is 0.60 ⁇ a ⁇ 0.90
- b is 0 ⁇ b ⁇ 0.30
- c is 0.05 ⁇ c ⁇ 0.25
- d is 4.75 ⁇ d ⁇ 5.20
- e is 0. 05 ⁇ e ⁇ 0.40
- a + b + c 1, and d + e is 5.10 ⁇ d + e ⁇ 5.35.
- a is 0.60 ⁇ a ⁇ 0.90
- b is 0 ⁇ b ⁇ 0.30
- c is 0.05 ⁇ c ⁇ 0.25
- d is 4.75 ⁇ d ⁇ 5.20
- e is 0.
- a, b, c, d and e represent the content ratio of each element by the atomic number ratio, and the details are as follows.
- the content ratio may be referred to as “content” or “amount”.
- La is effective in increasing the hydrogen storage amount
- a representing the La content in the formula (1) is 0.60 ⁇ a ⁇ 0.90.
- the lower limit of a is preferably 0.65 ⁇ a, more preferably 0.68 ⁇ a
- the upper limit of a is preferably a ⁇ 0.85. If it is less than the lower limit, the effect of increasing the hydrogen storage amount may not be expected, and if it exceeds the upper limit, the equilibrium pressure may be lowered.
- Ce is effective in increasing the equilibrium pressure
- b which represents the content of Ce in the formula (1), is 0 ⁇ b ⁇ 0.30.
- the lower limit of b is preferably 0 ⁇ b
- the upper limit of b is preferably b ⁇ 0.25, more preferably b ⁇ 0.22. If it exceeds the upper limit, the hysteresis of the PCT curve may decrease.
- Sm is effective in increasing the equilibrium pressure, and is also effective in showing a clear squareness in the PCT curve.
- C representing the content of Sm in the formula (1) is 0.05 ⁇ c ⁇ 0.25.
- the lower limit of c is preferably 0.07 ⁇ c, more preferably 0.10 ⁇ c, and the upper limit of c is preferably c ⁇ 0.23. If it is less than the lower limit, the effect of increasing the equilibrium pressure may not be expected, and the effect of showing a clear squareness of the PCT curve may not be obtained. If it exceeds the upper limit, the hydrogen storage amount may decrease. ..
- the squareness refers to how much shoulder (shoulder) the shape exhibits in the shape at the end of the PCT emission curve, and it is evaluated that the more clear the shoulder is, the better the squareness is.
- This alloy with good squareness shows the ability to release stored hydrogen at a constant release pressure until the end of release. The index of this angularity in the present application will be described later.
- Ni is effective in improving the durability of the hydrogen storage alloy according to the present invention, reducing hysteresis, and the like, and d representing the Ni content in the formula (1) is 4.75 ⁇ d ⁇ 5.20. Is.
- the lower limit of d is preferably 4.80 ⁇ d, and more preferably 4.85 ⁇ d. If it is less than the lower limit, the effect of improving the durability and the effect of reducing the hysteresis may not be expected, and if it exceeds the upper limit, the hydrogen storage amount may decrease.
- M is composed of Mn alone or two elements of Mn and Co, and is effective in reducing the hysteresis of the PCT curve.
- e representing the content of M is 0.05 ⁇ e ⁇ 0.40.
- the lower limit of e is preferably 0.07 ⁇ e.
- the upper limit of e is preferably e ⁇ 0.35, more preferably e ⁇ 0.32. If it is less than the lower limit, the effect of reducing the hysteresis of the PCT curve may not be expected, and if it exceeds the upper limit, the equilibrium pressure and the storage / release rate of hydrogen may decrease.
- d + e represents the total content of Ni and M. This value affects the hysteresis and hydrogen storage capacity of the PCT curve of the hydrogen storage material of the present invention, and by adjusting to the following range, it is possible to maintain a sufficient hydrogen storage capacity for hydrogen storage while using an alloy with a small PCT curve hysteresis. can do.
- d + e is 5.10 ⁇ d + e ⁇ 5.35, and the lower limit of d + e is preferably 5.12 ⁇ d + e.
- Sm and M in the formula (1) are elements that are effective in increasing the equilibrium pressure at the time of hydrogen storage and release, improving the squareness of the PCT curve, and reducing the hysteresis of the PCT curve, respectively. , A higher effect can be obtained by combining these elements.
- c + e is preferably 0.20 ⁇ c + e ⁇ 0.50, and more preferably 0.20 ⁇ c + e ⁇ 0.45.
- the elemental composition of the alloy of the present invention represented by the above formula (1) can be confirmed by quantitative analysis with an ICP (Inductively Coupled Plasma) analyzer.
- ICP Inductively Coupled Plasma
- the alloy of the present invention when referred to, it means an alloy having an elemental composition represented by the formula (1) unless otherwise specified.
- the alloy of the present invention may substantially contain unavoidable impurities such as those derived from raw materials.
- unavoidable impurities include, but are not limited to, Pr, Nd, Al and the like.
- the amount of unavoidable impurities in the alloy of the present invention is 0.5% by mass or less.
- the alloy of the present invention can be obtained, for example, as an alloy slab as described later, but the particle size of the crystals in the alloy slab is preferably 25 to 250 ⁇ m as an average particle size, and more preferably. It is 40 to 230 ⁇ m.
- the average particle size of the crystal can be measured as follows.
- the alloy slab is embedded in a room temperature curing type resin (for example, epoxy resin) and cured, and rough polishing and precision polishing are performed with a wet polishing machine, and finally the polished surface is finished to a mirror surface to form an alloy cross section.
- a room temperature curing type resin for example, epoxy resin
- the cross section of the alloy is etched with a 0.1 M nitrate aqueous solution, and then the lengths of the major axis and the minor axis orthogonal to the midpoint of each crystal in the visual field are measured using a polarizing microscope.
- “(Length of major axis + length of minor axis) / 2” is defined as the particle size of the crystal.
- the particle size of any three crystals is measured in this way, and the average value thereof is taken as the average particle size.
- the size of the alloy slab for measuring the crystal grain size is not particularly limited, but for example, an alloy slab of about 1 cm 3 may be used. Further, the crystal grain size may be measured using alloy flakes of about 1 cm square, and even in that case, the average grain size is preferably 25 to 250 ⁇ m.
- the alloy of the present invention has a hydrogen release pressure Pa1 at a hydrogen storage capacity of 0.3 wt% (weight)% and a hydrogen release at a hydrogen storage capacity of 0.1 wt% in a hydrogen pressure-composition isotherm diagram (PCT curve) at 20 ° C. It is preferable that the pressure P a2 satisfies the relational expression of [ ⁇ ln (P a1 ) -ln (P a2 ) ⁇ /0.2] ⁇ 1.40. Since the PCT curve has the above characteristics, the angularity of the curve becomes clear, and more hydrogen can be released when the hydrogen release is terminated at a predetermined pressure, so that the stored hydrogen is effectively left in the alloy.
- the hydrogen release pressure measurement points between 0.08 wt% and 0.12 wt% of the hydrogen storage amount are two or more points in order to obtain Pa2 .
- the alloy of the present invention has a hydrogen release pressure P a1 at a hydrogen storage capacity of 0.3 wt% and a hydrogen release pressure P a3 at a hydrogen storage capacity of 1.1 wt%. It is preferable to satisfy the relational expression of ⁇ ln (P a3 ) -ln (P a1 ) ⁇ / 0.8] ⁇ 0.35, and [ ⁇ ln (P a3 ) -ln (P a1 ) ⁇ / 0.8]. It is more preferable to satisfy the relational expression of ⁇ 0.28.
- the hydrogen storage pressure P b1 and the hydrogen release pressure P b2 at a hydrogen storage capacity of 0.8 wt% are ln (P b1 / P b2 ) ⁇ 0. It is preferable to satisfy the relational expression of .43.
- the relationship between the hydrogen storage pressure and the hydrogen release pressure satisfies the above equation, the hysteresis is small, so that it is not necessary to generate a large pressure difference or temperature difference between the storage and release of hydrogen, and the efficiency is improved. Good driving is possible.
- the relationship of the above equation is used as an index of "hysteresis of PCT curve".
- the hydrogen release pressure P b2 at a hydrogen storage capacity of 0.8 wt% is preferably 0.05 MPa or more, more preferably 0.07 MPa or more in the hydrogen pressure-composition isotherm diagram at 20 ° C. This is because hydrogen release in the temperature range of normal temperature to 95 ° C. is better. There is no particular upper limit for P b2 , but it is substantially 1.00 MPa at 20 ° C.
- alloys of the present invention constituting the hydrogen storage material of the present invention satisfy the above relationship in the PCT curve, but a part of the alloy may satisfy the above relationship.
- a method for producing the hydrogen storage material of the present invention will be described.
- a method for preparing an alloy for example, a strip casting method such as a single roll method, a double roll method or a disk method, or a mold casting method can be mentioned.
- the strip casting method raw materials blended so as to have a desired alloy composition are prepared. Then, in an inert gas atmosphere such as Ar, the blended raw materials are heated and melted to form an alloy melt, and then the alloy melt is poured into a copper water-cooled roll and rapidly cooled and solidified to obtain an alloy slab. .. Further, in the mold casting method, after the alloy melt is obtained in the same manner, the alloy melt is poured into a water-cooled copper (or iron) mold, cooled and solidified to obtain an ingot.
- the cooling rate differs between the strip casting method and the mold casting method, and in general, the strip casting method is preferable when an alloy having a small segregation and a uniform composition distribution can be obtained. Since the alloy of the present invention constituting the hydrogen storage material of the present invention is preferably an alloy having less segregation and a uniform composition distribution, the strip casting method is the preferred method in the present invention.
- the cooling rate of the alloy melt when manufacturing alloy slabs is controlled as follows. That is, the cooling rate from the cooling start temperature of the alloy melt (for example, the temperature at the time when the molten metal comes into contact with the roll) to the alloy temperature reaching 1000 ° C. is set to 300 ° C./sec or more. It is preferably 700 ° C./sec or higher, more preferably 1000 ° C./sec or higher, and particularly preferably 4000 ° C./sec or higher. There is no particular upper limit to the cooling rate, but it is actually about 20000 ° C./sec or less.
- the cooling start temperature of the alloy melt varies depending on the alloy composition, but is in the range of about 1300 to 1500 ° C.
- the cooling rate of less than 1000 ° C. is not particularly limited.
- the alloy slab may be recovered at a temperature of 100 ° C. or lower by allowing it to cool after peeling from the roll.
- the heat treatment can be performed in the range of 700 ° C. or higher and 1200 ° C. or lower in an atmosphere of an inert gas 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, preferably 3 hours or more and less than 15 hours.
- the pulverization can be performed using a known pulverizer.
- the particle size of the alloy powder is preferably 800 ⁇ m or less, more preferably 500 ⁇ m or less.
- the lower limit of the particle size of the alloy powder does not need to be specified, but is substantially about 0.1 ⁇ m.
- the particle size of the alloy powder refers to the diameter measured by a sieve shaker (low tap type).
- the hydrogen storage material of the present invention may be the alloy itself powdered in this way, a composite obtained by mixing the alloy powder and a resin or the like and molded into an arbitrary shape such as granules, or temperature control is possible. It may be a complex immobilized on an object.
- the resin functions as a binder for the alloy powder.
- Mixing can be done by a known method.
- the mixture can be mixed by a mortar, a rotary type mixer such as a double cone and a V type, a stirring type mixer such as a blade type and a screw type, and the like. It is also possible to use a crusher such as a ball mill or an attritor mill to crush and mix the alloy slab and the binder.
- the hydrogen storage container of the present invention is provided with the hydrogen storage material produced as described above, and a known material and shape of the container can be used.
- the hydrogen supply device of the present invention is provided with the hydrogen storage container, and other known configurations can be used.
- alloy of the present invention of the example and the alloy of the non-invention of the comparative example are referred to as "alloy”.
- alloy slab an alloy obtained in the form of a slab by the strip casting method
- a crushed alloy slab is referred to as an alloy powder.
- Example 1 The raw metal was weighed so that the elemental composition of the finally obtained alloy had the composition shown in Table 1, and melted in an argon gas (Ar) atmosphere in a high-frequency melting furnace to obtain an alloy melt. Subsequently, the molten material was rapidly cooled and solidified by a strip casting method using a single roll casting device using a copper water-cooled roll at a pouring temperature of 1500 ° C. to produce an alloy slab having an average thickness of about 0.3 mm. Obtained.
- the cooling start temperature of the alloy melt that is, the temperature at the time of contact with the copper water-cooled roll was about 1450 ° C. There was a difference in the cooling rate between the roll contact side and the non-contact side of the alloy melt, and the cooling rate from 1450 ° C. to 1000 ° C. was between 6000 ° C./sec and 9000 ° C./sec.
- the alloy slab obtained above was heat-treated in an Ar atmosphere at 1030 ° C. for 10 hours in a heat treatment furnace.
- the alloy slab after the heat treatment was embedded in an epoxy resin and cured, and rough polishing and precision polishing were performed with a wet polishing machine, and finally the polished surface was finished to a mirror surface to form an alloy cross section.
- the average particle size of the crystals was measured by the above method using a polarizing microscope (manufactured by Olympus Co., Ltd.). The average particle size was 110 ⁇ m.
- the alloy slab after the heat treatment was crushed in a stainless steel mortar, and a sieve having a mesh size of 500 ⁇ m was used to obtain an alloy powder having a pass of 500 ⁇ m.
- the hydrogen storage and release characteristics of the obtained alloy powder were measured using a PCT measurement automatic high-pressure Sieberts device (manufactured by Hughes Technonet Co., Ltd.) to obtain a PCT curve.
- the PCT measurement was performed by vacuuming at 80 ° C for 1 hour with an automatic high-pressure Sieberts device (manufactured by Hughes Technonet Co., Ltd.) (vacuum degree: about 0.5 to 2.5 Pa), and then about 2.5 MPa. It was pressurized with hydrogen pressure, and finally hydrogen was occluded at 0 ° C. until the hydrogen pressure became stable. Subsequently, the vacuum is similarly evacuated at 80 ° C.
- FIG. 1 shows a hydrogen pressure-composition isotherm diagram (PCT curve).
- Table 1 shows the results of reading the hydrogen storage amount at a hydrogen storage pressure of 1.0 MPa and the hydrogen release pressure at a hydrogen storage amount of 0.8 wt% from the obtained PCT curve.
- Examples 2 to 11 and 13 The alloy slabs and alloy powders of each example were prepared in the same manner as in Example 1 except that the elemental composition of the finally obtained alloy was changed as shown in Table 1, and the hydrogen storage and release characteristics (squareness, etc.) were obtained. Measurements were made.
- the pouring temperature, cooling start temperature and cooling rate of the alloy melts of these examples were almost the same as those of Example 1 at 1500 ° C., 1450 ° C., and between 6000 ° C./sec and 9000 ° C./sec. ..
- the results are shown in Table 1.
- the hydrogen pressure-composition isotherm diagram (PCT curve) of Example 4 is shown in FIG.
- the average particle sizes of the crystals of Examples 2, 4 and 6 were 96 ⁇ m, 85 ⁇ m, and 105 ⁇ m, respectively.
- Example 12 The raw metal was weighed so that the elemental composition of the finally obtained alloy had the composition shown in Table 1, and melted in an argon gas (Ar) atmosphere in a high-frequency melting furnace to obtain an alloy melt. Subsequently, the molten metal was cast at an iron mold (mold casting) at a pouring temperature of 1500 ° C. to obtain an alloy ingot having a thickness of about 25 mm. An alloy powder was prepared in the same manner as in Example 1, and the hydrogen storage and release characteristics (squareness, etc.) were measured. The cooling start temperature of the alloy melt, that is, the temperature at the time of contact with the iron mold was about 1450 ° C. The cooling rate of the alloy melt was about 5 ° C./sec. The results are shown in Table 1. The hydrogen pressure-composition isotherm diagram (PCT curve) of Example 12 is shown in FIG. The average particle size of the crystals of Example 12 was 749 ⁇ m.
- the alloy of each example has a better squareness of the PCT curve than the alloy of each comparative example, shows a sufficient hydrogen storage capacity, and exhibits hydrogen in the temperature range of normal temperature to 95 ° C. It is fully possible to store and release. Further, it can be seen that an excellent hydrogen storage material having a small hysteresis of the PCT curve can be obtained. Moreover, it is inexpensive because the amount of Co used is suppressed.
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Abstract
Description
なお、上記の式の関係を「PCTカーブのヒステリシス」の指標とする。
最終的に得られる合金の元素組成が表1に示す組成になるよう原料金属を秤量し、高周波溶解炉にてアルゴンガス(Ar)雰囲気中で溶解し、合金溶融物とした。続いて、この溶融物の注湯温度を1500℃として、銅製水冷ロールを用いた単ロール鋳造装置によるストリップキャスト法にて急冷・凝固し、平均の厚みが約0.3mmである合金鋳片を得た。合金溶融物の冷却開始温度、すなわち銅製水冷ロールに接触する時点の温度は1450℃程度であった。合金溶融物のロール接触側と非接触側では冷却速度に差があり、1450℃から1000℃までの冷却速度は、6000℃/秒から9000℃/秒の間であった。
最終的に得られる合金の元素組成を表1の通りに変更した以外は、実施例1と同様に各実施例の合金鋳片及び合金粉末を作製し、水素吸蔵放出特性(角形性等)の測定を行った。これらの実施例の合金溶融物の注湯温度、冷却開始温度及び冷却速度は、実施例1とほぼ同じの、1500℃、1450℃、及び6000℃/秒から9000℃/秒の間であった。結果を表1に示す。実施例4の水素圧力-組成等温線図(PCTカーブ)を図2に示す。実施例2、4及び6の結晶の平均粒径は、各々96μm、85μm、及び105μmであった。
最終的に得られる合金の元素組成が表1に示す組成になるよう原料金属を秤量し、高周波溶解炉にてアルゴンガス(Ar)雰囲気中で溶解し、合金溶融物とした。続いて、この溶融物の注湯温度を1500℃として、鉄鋳型にて鋳造を行い(金型鋳造)、厚みが約25mmである合金塊を得た。実施例1と同様に合金粉末を作製し、水素吸蔵放出特性(角形性等)の測定を行った。合金溶融物の冷却開始温度、すなわち鉄鋳型に接触する時点の温度は1450℃程度であった。合金溶融物の冷却速度は約5℃/秒であった。結果を表1に示す。実施例12の水素圧力-組成等温線図(PCTカーブ)を図2に示す。実施例12の結晶の平均粒径は749μmであった。
最終的に得られる合金の元素組成を表1の通りに変更した以外は、実施例1と同様に各比較例の合金鋳片及び合金粉末を作製し、水素吸蔵放出特性(角形性等)の測定を行った。これらの比較例の合金溶融物の注湯温度、冷却開始温度及び冷却速度は、実施例1とほぼ同じの、1500℃、1450℃、及び6000℃/秒から9000℃/秒の間であった。結果を表1に示す。比較例1の水素圧力-組成等温線図(PCTカーブ)を図1に示す。
Claims (5)
- 前記合金において、c+eが0.20≦c+e≦0.50である、
請求項1に記載の水素貯蔵材料。 - 前記合金の20℃における水素圧力-組成等温線図において、水素吸蔵量0.3wt%における水素放出圧Pa1と水素吸蔵量0.1wt%における水素放出圧Pa2が、[{ln(Pa1)-ln(Pa2)}/0.2]≦1.40の関係式を満たす、
請求項1又は2に記載の水素貯蔵材料。 - 請求項1~3のいずれか一項に記載の水素貯蔵材料を備える水素貯蔵容器。
- 請求項4に記載の水素貯蔵容器を備える水素供給装置。
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