US20080089834A1

US20080089834A1 - Reactive Working Material for Use in Hydrogen Production by Decompostion of Water

Info

Publication number: US20080089834A1
Application number: US11/662,127
Authority: US
Inventors: Tatsuya Kodama; Hidemasa Ando; Yukiko Hashimoto
Original assignee: Individual
Current assignee: Krosaki Harima Corp
Priority date: 2004-09-07
Filing date: 2004-09-07
Publication date: 2008-04-17
Also published as: JPWO2006027829A1; AU2004323089B2; JP4681560B2; AU2004323089A1; US20100119441A1; US8110174B2; WO2006027829A1; AU2004323089B8

Abstract

Disclosed is a reactive working material for use in a process of producing hydrogen by splitting water based on a two-step thermochemical water-splitting cycle through the utilization of solar heat, industrial waste heat or the like, which comprises a ferrite fine powder and a cubic zirconia supporting the ferrite fine powder. This reactive working material makes it possible to prevent scaling off of the ferrite fine powder from the zirconia fine powder due to volumetric changes of the ferrite fine powder during repeated use, and suppress growth of FeO grains due to repetition of melting and solidification when used as a reactive working material for a cyclic reaction under a high temperature of 1400° C. or more.

Description

TECHNICAL FIELD

The present invention relates to a technique of producing hydrogen by splitting water through the utilization of solar heat, industrial waste heat or the like, and more particularly to a hydrogen production process based on a two-step thermochemical water-splitting cycle and a reactive working material for use in the hydrogen production process.

BACKGROUND ART

A hydrogen production process based on a two-step thermochemical water-splitting cycle has been widely known before the filing of this patent application. The hydrogen production process is designed to repeat the following two reaction formulas.
MOox→MOred+½O₂ First Step
MOred+H₂O→MOox+H₂ Second Step
Specifically, this hydrogen production process comprises a first step of reducing a metal oxide MOox to form a reduced metal oxide MOred and produce oxygen through a high-temperature thermal decomposition reaction, and a second step of reacting the reduced metal oxide with water to oxidize the reduced metal oxide to a metal oxide and produce hydrogen.
Typically, magnetite Fe₃O₄, which is known and described as “iron-based oxide” or “ferrite”, is used as the metal oxide MOox, i.e., a reactive working material for the hydrogen production process. This iron-based oxide as the reactive working material is reduced to wustite FeO in the first step to release oxygen, and the wustite FeO is reacted with water in the second step to release hydrogen and return to magnetite Fe₃O₄. Then, the reactive working material will be reused.
In the above reaction formulas, the process of releasing oxygen in the first step is generally required to perform under a high-temperature atmosphere of 1800 to 2300° C. In practice, under such a high-temperature atmosphere for the oxygen release reaction, the iron-based oxide is sintered to be deactivated and cause quite strong vaporization. Therefore, it is required to quench the vaporized substance, and this requirement makes it difficult to put the two-step thermochemical water-splitting cycle to practical use.
With a view to solve the problem concerning the reactive working material for use in the hydrogen production process based on the two-step thermochemical water-splitting cycle, the applicant of this patent application previously disclosed a hydrogen production-process based on a two-step thermochemical water-splitting cycle which uses a reactive working material comprising ferrite fine powder and zirconia fine powder supporting the ferrite fine powder, in Japanese Patent Application No. 2003-060101.
This reactive working material is formed such that ferrite fine powder is supported on zirconia fine powder. The zirconia fine powder is hardly sintered even at high temperatures, and the ferrite fine particles supported on the zirconia fine powder is prevented from coming in close contact with other ferrite particles each other so as to suppress grain growth thereof to provide enhanced reactivity and reusability even at a relatively low temperature of 1400° C. or less.
Fe₃O₄and FeO to be repeatedly formed during the reaction cycle have specific gravities of 5.2 and 5.7, respectively. Thus, due to volumetric changes of these powders during the reaction cycle, the ferrite fine powder will scale off from the zirconia fine powder to spoil the zirconia powder's effect of suppressing grain growth in the ferrite fine powder., Moreover, under a reaction atmosphere repeatedly having a temperature of 1400° C. or more which is greater than a melting point of FeO, the ferrite fine powder will be gradually agglomerated to cause grain growth while repeating melting and solidification, resulting in deterioration of reaction efficiency.

DISCLOSURE OF THE INVENTION

In a reactive working material for use in a hydrogen production process based on a two-step thermochemical water-splitting cycle, which comprises ferrite and zirconia supporting the ferrite, it is an object of the present invention to provide an effective means for preventing the ferrite from scaling off the zirconia due to volumetric changes of the ferrite during repeated use.
It is another object of the present invention to provide a means for suppressing growth of FeO grains due to repetition of melting and solidification when used as a reactive working material for a cyclical reaction under a high temperature of 1400° C. or more.
In order to achieve the above objects, the present invention provides a reactive working material for use in a two-step thermochemical water-splitting cycle, which comprises ferrite and zirconia supporting the ferrite, wherein the zirconia supporting ferrite is a cubic zirconia.
As used in this specification, the “ferrite” means an oxide represented by a composition formula of M(II)O.Fe₂O₃, wherein M(II) is a divalent metal, such as Fe, Mn, Co, Mg, Ni, Zn or Cu. The oxide constituting the ferrite may have any configuration. For example, Fe₃O₄having a spinel crystal structure may be used. The divalent metals, such as Mn, Co or Mg, may be effectively doped as ions by replacing ferrous ion in Fe₃O₄partially or all. When used in the form of a fine powder, the ferrite is prepared to have a particle size, preferably, of 10 μm or less, more preferably 1 μm or less.
Further, the “cubic zirconia” means a fully-stabilized zirconia or a partially-stabilized zirconia which contains a stabilizer, such as calcia or yttria, and a zirconia including a cubic crystal phase. Preferably, the cubic zirconia contains yttria or calcia in an amount of 2 mol % or more. If the content rate of the stabilizer is less than 2 mol %, the suppression of grain growth in the ferrite will become insufficient. An excessive content rate of the stabilizer causes deterioration in reactivity. Thus, more preferably, an upper limit of the content rate is set at 25 mol % or less.
In the present invention, the reactive working material comprising a ferrite and a zirconia supporting the ferrite may be formed as a ferrite/zirconia composite powder. Alternatively, the reactive working material may be formed as a ferrite-supporting porous zirconia ceramics. In this case, a ferrite fine powder may be coated on, i.e., supported on, a porous structure of a porous zirconia ceramics.
The ferrite/zirconia composite powder may be prepared by the following specific method.
As one example, a method using an aqueous Fe(II) salt solution may be employed. Specifically, an yttria fully-stabilized or partially stabilized zirconia fine powder or a calcia fully-stabilized or partially stabilized zirconia fine powder which has a particle size of 10 μm or less, preferably 1 μm or less, is dispersed in an aqueous Fe(II) salt solution or an aqueous Fe(II) salt solution containing another metal salt dissolved therein as a doping metal [M(II)], and an aqueous alkali hydroxide solution is added to the zirconia fine powder-dispersed aqueous solution to form a Fe (II) hydroxide colloid therein. Then, air is bubbled in the colloid-containing aqueous solution to oxidize the Fe (II) hydroxide colloid. Then, a dissolution-precipitation reaction where the Fe (II) hydroxide colloid is dissolved in the zirconia fine powder-dispersed aqueous solution and then precipitated as a ferrite is promoted to grow Fe₃O₄or M_xFe_3-xO₄on the dispersed zirconia fine powder so as to form a ferrite/zirconia composite powder.
The porous zirconia ceramics supporting the ferrite may be prepared by immersing a porous zirconia ceramics including a cubic crystal phase into the above aqueous Fe(II) salt solution or the above aqueous Fe(II) salt solution containing another metal salt dissolved therein as a doping metal [M(II)], drying the pulled-out porous zirconia ceramics body, and subjecting the dried porous zirconia ceramics to a heat treatment. In the same manner, a reactive working material having a ferrite fine powder coating can be prepared using a cubic zirconia having any other configuration.
As another method for preparing the ferrite/zirconia composite powder, a solvent impregnation process may be used. Specifically, a fully-stabilized or partially-stabilized zirconia fine powder is dispersed in an aqueous solution of a metal salt, such as iron nitrate, iron chloride or organic iron, and a salt of the doping metal. The obtained mixture is evaporated and dried, and then the dried mixture is burnt to allow the metal salt on the zirconia to be decomposed to the metal oxide. Then, the metal oxide is heated under a H₂/H ₂ 0 mixed gas atmosphere or a CO/CO₂mixed gas atmosphere at a temperature of 300° C. or more.
The porous zirconia ceramics supporting the ferrite may be prepared by immersing a porous zirconia ceramics including a cubic crystal phase into the above aqueous Fe(II) salt solution or the above aqueous Fe(II) salt solution containing another metal salt dissolved therein as a doping metal [M(II)], drying the pulled-out porous zirconia ceramics body, and subjecting the dried porous zirconia ceramics to a heat treatment. In the same manner, a reactive working material having a ferrite fine powder coating can be prepared using a cubic zirconia having any other configuration.
When a reaction temperature is increased up to 1300 to 1500° C., the ferrite fine powder supported on the zirconia is formed as FeO through release of oxygen therefrom. Subsequently, when the reaction temperature is decreased to 1000° C. and water vapor is introduced, FeO returns to the original Fe₃O₄through oxidization while decomposing water to generate hydrogen.
In the above process using the fully-stabilized cubic zirconia, during the course of the formation of FeO at the high temperatures, FeO is incorporated into the zirconia as a solid solution to form a cubic zirconia containing iron ions in the zirconia lattice. In this case, even during the course of the oxidization to Fe₃O₄as well as that of the thermal reduction of Fe₃O₄, it is impossible that FeO particles supported on the zirconia fine power scale off the zirconia support and exist as independent grains since FeO phase is not formed anymore as the reduced iron-based oxide.
In the partially-stabilized cubic zirconia, while tetragonal and monoclinic crystal phases exist as a zirconia crystal together with a cubic crystal phase, the zirconia formed as a solid solution with FeO stabilizes the cubic crystal phase to allow the entire crystal phase to have a transition to a cubic zirconia.
As above, at a high reaction temperature of 1300 to 1500° C., Fe₃O₄and cubic zirconia are changed to FeO-zirconia solid solutions through release of oxygen therefrom. Then, when the reaction temperature is reduced to 1000° C. and water vapor is introduced, iron ions in the solid solution of the cubic stabilized zirconia are oxidized while generating hydrogen, and a Fe₃O₄fine powder is precipitated on the cubic zirconia.
That is, in the hydrogen production process based on the two-step thermochemical water-splitting cycle, a first step where a solid solution of FeO and cubic zirconia is formed at high temperatures, and a second step where a Fe₃O₄fine powder is precipitated from the solid solution of cubic zirconia incorporating iron ions and formed directly on the cubic zirconia during decomposition of water at low temperatures, will be repeatedly performed.
A temperature allowing the cubic solid solution of FeO and zirconia to be fully molten is 2000° C. or more when a ratio of FeO to the solid solution is 30 wt % or less. Thus, the solid grains are not excessively molten during the cyclic reaction, and grain growth is suppressed. That is, FeO is not changed to independent grains, and therefore an undesirable situation where FeO grains are molten and agglomerated at about 1400° C., i.e., a melting point thereof, can be avoided to suppress grain growth.
In addition, FeO incorporated in the zirconia as a solid solution is penetrated into and strongly bonded with the zirconia crystal to eliminate the problem about scaling off of the ferrite fine grains from the zirconia fine grains due to volumetric changes, i.e., a large difference in specific gravity between Fe₃O₄as a reactive working material and FeO to be formed through the reaction.
Thus, a fully-stabilized or partially-stabilized cubic zirconia used as a zirconia fine powder for supporting a ferrite fine powder makes it possible to eliminate the problem about scaling off of the ferrite fine powder from the zirconia fine powder as in a case of using a monoclinic zirconia as a support, and achieve an effect of preventing excessive sintering of the ferrite fine powder.
In the present invention, a hydrogen production process using the ferrite supported on the fully-stabilized or partially-stabilized zirconia is performed according to the following reaction formulas.
In the use of an yttria fully-stabilized or partially-stabilized zirconia: $\begin{matrix} \begin{matrix} x / 3 {Fe}_{3} O_{4} + Y_{y} {Zr}_{1 - y} O_{2 - y / 2} (cubic crystal phase, \\ or cubic crystal phase + tetragonal crystal phase) \\ = {Fe}_{x} Y_{y} {Zr}_{1 - y} O_{2 - y / 2 + x} (cubic crystal phase) + x / 6 O_{2}; \\ and \end{matrix} & Formula (1) \\ \begin{matrix} {Fe}_{x} Y_{y} {Zr}_{1 - y} O_{2 - y / 2 + x} (cubic crystal phase) + x / 3 H_{2} O \\ = x / 3 {Fe}_{3} O_{4} + Y_{y} {Zr}_{1 - y} O_{2 - y / 2} (cubic crystal phase) + x / 3 H_{2} \end{matrix} & Formula (2) \end{matrix}$
In the use of a calcia fully-stabilized or partially-stabilized zirconia: $\begin{matrix} \begin{matrix} x / 3 {Fe}_{3} O_{4} + {Ca}_{y} {Zr}_{1 - y} O_{2 - y} (cubic crystal phase, \\ o r a combination of cubic crystal phase + \\ monoclinic crystal phase + tetragonal crystal phase) \\ = {Fe}_{x} {Ca}_{y} {Zr}_{1 - y} O_{2 - y + x} (cubic crystal phase) + x / 6 O_{2}; \\ and \end{matrix} & Formula (3) \\ {Fe}_{x} {Ca}_{y} {Zr}_{1 - y} O_{2 - y + x} (cubic crystal phase) + x / 3 H_{2} O & Formula (4) \\ = x / 3 {Fe}_{3} O_{4} + {Ca}_{y} {Zr}_{1 - y} O_{2 - y} (cubic crystal phase) + x / 3 H_{2} \end{matrix}$
The present invention provides the following advantages.
A crystal growth of the iron-based oxide as the reactive working material can be suppressed to maintain cyclical reactivity.
The oxygen-releasing temperature is reduced in the second reaction step since the grain growth of the iron oxide particles is effectively suppressed. This lower reaction temperature makes it possible to eliminate the need for quenching of the reactive working material and a large-scale facility for the quenching.
Thus, a process of converting natural heat energy, such as solar heat, to chemical energy of hydrogen can be achieved.

BEST MODE FOR CARRYING OUT THE INVENTION

An embodiment of the present invention will now be described based on the following Example.

EXAMPLE 1

An yttria partially-stabilized zirconia (YSZ) represented by (ZrO₂)_0.97(Y₂O₃)_0.03and a calcia partially-stabilized zirconia (CSZ) represented by (ZrO₂)_0.97(CaO)_0.03(produced by Kojundo Chemical Lab. Co. Ltd.) were used as a support of a ferrite. Each of the YSZ and CSZ has a particle size of 1 μm or less. The YSZ primarily comprises a cubic crystal phase and slightly has a tetragonal crystal phase. The YSZ has a BET (Brunauer-Emmett-Teller) surface area of 7.7 m²g⁻¹. The CSZ primarily comprises a cubic crystal phase and partially has a monoclinic crystal phase. As Comparative Example, a conventional monoclinic zirconia (BET surface area: 12.6 m²g⁻¹) was used as a support.
A cubic zirconia-supported ferrite as Inventive Example and a monoclinic zirconia-supported ferrite as Comparative Example were prepared through the following process.
The zirconia particles were suspended in distilled water after removing oxygen and CO₂therefrom, and N₂was supplied therethrough for 1 hour to expel any remaining air. Then, a given amount of FeSO₄, MnSO₄and CoSO₄were dissolved in the suspension, and 0.15 mol dm⁻³of NaOH solution was added to the obtained solution to adjust pH at 8.5 so as to form hydroxides of Fe²⁺, Mn²⁺and Co²⁺. A mass ratio of a ferrite phase to the zirconia is set in the range of 20 to 25%. This mixed solution was heated up to 65° C., and then an NaOH solution was added to the heated solution while supplying air bubbles therethrough, to maintain pH at 8.5. A resulting product was collected by centrifugal separation at 14000 rpm. The collected product was rinsed with distilled water and acetone, and then dried at room temperature all day and night. In advance of a high-temperature reaction, the sample prepared in the above manner was subjected to a high-temperature stabilization treatment under an N₂atmosphere at 900° C. Additionally, as Comparative Example, Fe₃O₄without a zirconia support was prepared through a coprecipitation process.
The obtained samples were identified using an X-ray diffractometer (XRD) (RAD-γ A diffractometer: produced by Rigaku Co. Ltd.). A ferrite phase in each of the samples was dissolved by HCl, and respective amounts of Fe, Mn and Co in the solution were analyzed through inductively coupled plasma (ICP) emission spectrometry (SPS-1500 V: SEIKO Instruments Inc.) to determine a weight ratio of ferrite/zirconia support.
Each of the samples was used in the water-decomposition reaction represented by the aforementioned formulas (1) and (2) or (3) and (4). The reaction represented by the formula (1) or (3) and the reaction represented by the formula (2) or (4) will hereinafter referred to respectively as “thermal reduction reaction” and “water-decomposition reaction”.
FIG. 1 shows an experimental apparatus for the thermal reduction reaction, which is designed to supply N₂gas to a silica tube 4 which is contained in an infrared furnace 1 to house a platinum cup 2 for receiving the solid sample 3 therein, and exhaust the N₂gas from the silica tube 4.
The solid sample (about 1 g) 3 was put in the platinum cup (diameter: 10 mm, depth: 7 mm) 2, and set in the silica tube (SSA-E45; produced by ULVAC-RIKO, Inc) 4 having an inner diameter of 45 mm. N₂gas (purity: 99.999%) was supplied at a flow rate of 1.0 Ndm³·min. A temperature of the platinum cup 2 was controlled using an R-type thermocouple 5 disposed in contact with the platinum cup 2 in the infrared furnace (RHL-VHT-E44: produced by ULVAC-RIKO, Inc) 1, and increased up to a given temperature (1400° C.) so as to induce the thermal reduction reaction.
The solid sample 3 was heated at a constant temperature for 0.5 hours, and then cooled to room temperature. After completion of the reaction, the thermally reduced solid sample 3 was crushed using a mortar, and the obtained powder was put in the silica tube 4. Then, H₂O/N₂mixed gas was introduced into the reaction system to induce the water-decomposition reaction. The H₂O/N₂mixed gas was supplied at a flow rate of 4 Ncm³·min⁻¹through distilled water having a temperature of 80° C. In this process, a partial pressure of water vapor in the H₂O/N₂mixed gas was estimated as 47% from a vapor pressure at 80° C. and 1 atm.
The reaction system was heated up to 1000° C. within 10 minutes using an infrared furnace (RHL-E45P: produced by ULVAC-RIKO, Inc) 1, and then the water-decomposition reaction was promoted at a constant temperature of 1000° C. for 50 minutes.
In order to measure an amount of hydrogen generated through the water-decomposition reaction, the discharged gas was collected over water to a container. After completion of the water-decomposition reaction, a volume of the collected discharged gas was measured, and gas components were determined using a thermal conductivity detector (TCD) gas chromatography (GC-4C: produced by Shimadzu Corp.). Each of the samples was identified using the XRD (RAD-γ A diffractometer: produced by Rigaku Co. Ltd.).
Further, in order to check repeatability of the cyclical reaction, the thermal reduction reaction and the water-decomposition reaction using the ferrite/zirconia composite powder were alternately repeated two to seven times. After completion of each cycle, the thermally reduced sample was crushed using a mortar.
FIGS. 2(a) and 2(b) show respective XRD patterns of the YSZ supporting 20 wt % of Fe₃O₄in two reaction stages, wherein FIG. 2(a) shows an XRD pattern before initiation of the reaction, and FIG. 2(b) shows an XRD pattern after completer of the high-temperature thermal reduction reaction at 1400° C.
As shown in FIGS. 2(a) and 2(b), a strong peak of a cubic ZrO₂was observed together of a peak due to the reflection of Fe₃O₄. Further, a slight tetragonal crystal phase was observed in a part of the ZrO₂phase of the YSZ.
For comparison, this YSZ-supported Fe₃O₄and Fe₃O₄itself without the YSZ support were thermally reduced at 1400° C.
After the thermal reduction, the YSZ-supported Fe₃O₄was formed as porous pellets in the platinum cap. This pellet was easily crushed using the mortar, which was significantly effective in using for generating hydrogen in the subsequent water-decomposition reaction. In contract, the Fe₃O₄without the YSZ support was severely sintered in the platinum cap, and formed as a dense, hard, candy-like glossy agglomerate. The agglomerate was attached onto a bottom surface of the platinum cap. It was assumed that the sample is molted once at the high temperature and then cooled and solidified again. The reason is that the thermal reduction reaction temperature of 1400° C. is close to a melting point (1370° C.) of the reduced Fe₃O₄phase. This agglomerate was hardly crushed using the mortar, and therefore the subsequent water-decomposition reaction could not be performed using the Fe₃O₄without the YSZ support. These test results show that the YSZ support can effectively suppress sintering of an iron oxide at high temperatures.
FIG. 3 shows a hydrogen generation rate per gram of the sample and a water-decomposition temperature in the 1st cycle of the water-decomposition reaction, which represents a hydrogen generation profile in the water-decomposition reaction using the YSZ supporting Fe₃O₄(20 wt %) thermally reduced at a reaction temperature of 1400° C. by plotting a hydrogen generation rate (Ncm³·min⁻¹per gram of the sample with respect to a reaction time.
Further, the two-step water-splitting reaction using the Fe₃O₄/YSZ reactive working material was repeated seven times to check repeatability of the cyclical reaction.
FIG. 4 shows a measurement result of a hydrogen generation amount per gram of the reactive working material sample in each cycle. The repeatability was checked using two samples having a Fe₃O₄weight ratio of 20 wt % and 25 wt %. In FIG. 4, the sample having 20 wt % of Fe₃O₄and the sample having 25 wt % of Fe₃O₄are indicated by a black circle and a while circle, respectively. As seen in FIG. 4, a hydrogen generation amount in each of the samples is maintained at an approximately constant value even if the number of cycles is increased. Further, a hydrogen generation amount is drastically increased in most of the cycles by increasing the Fe₃O₄weight ratio from 20 wt % to 25 wt %.
A rate of Fe³⁺in Fe₃O₄which is reduced to Fe²⁺in the thermal reduction reaction will hereinafter be referred to as “Fe₃O₄conversion rate”. Then, the Fe₃O₄conversion rate was roughly estimated on the assumption that “Fe²⁺generated through the thermal reduction reaction will be entirely re-oxidized to Fe³⁺through the water-decomposition reaction”.
Table 1 shows a Fe₃O₄conversion rate in each of the seven cycles of the thermal reduction reaction, according to the above rough estimation. As seen in Table 1, when 20 wt % of Fe₃O₄is supported, 20 to 30% of the Fe₃O₄phase is converted to a reduced phase. Further, when the content rate of Fe₃O₄is increased to 25 wt %, the Fe₃O₄conversion rate is increased to about 30 to 40%.
In Table 2, given that a sample having Fe₃O₄supported on the YSZ is expressed as Fe₃O₄/YSZ; a sample having Co or Mn-doped Fe₃O₄supported on the YSZ is expressed as Co_xFe_3-xO₄/YSZ or Mn_xFe_3-x 0 ₄/YSZ; a sample having Fe₃O₄supported on the CSZ is expressed as Fe₃O₄/CSZ; and a sample having Fe₃O₄supported on the monoclinic zirconia is expressed as Fe₃O₄/monoclinic zirconia, respective hydrogen generation amounts (Ncm³g⁻¹) in these samples are compared with each other. While hydrogen is continuously generated in each of the samples, the hydrogen generation amount in the Fe₃O₄/monoclinic zirconia is sharply reduced in and after the 5th cycle. In contract, such a decrease in the hydrogen generation amount is not observed in the samples having the cubic zirconia support, i.e., the Fe₃O₄/YSZ and the Fe₃O₄/CSZ. The reason would be that grain growth due to the high-temperature reaction cycles is suppressed in the cubic zirconia-supported ferrite as compared with the monoclinic zirconia-supported ferrite.
FIGS. 5(a) to 5(d) show an SEM image (×1000) of the Fe₃O₄/YSZ and element mappings of the sample after the 7th cycle using an electron probe microanalyzer (EPMA), wherein FIG. 5(a) shows the sample before the reaction, and FIG. 5(b) shows the sample after the 7th cycle. FIG. 5(c) is a photograph showing a Fe distribution, and FIG. 5(d) a photograph showing a Zr distribution.
FIGS. 6(a) to 6(d) show an SEM image of the Fe₃O₄/monoclinic zirconia and Fe and Zr distributions after the 6th cycle using the EPMA.
As is clear from the comparison between the SEM images in these figures, while a Fe₃O₄grain in the Fe₃O₄/monoclinic zirconia grows to have a size equivalent to that of a ZrO₂grain in the 6th cycle, such a large grain growth is not observed in the Fe₃O₄/YSZ even after the 7th cycle, and the Fe₃O₄grain has a size of 2.5 μm or less. Further, it can be observed that there are many overlapped regions between the ZrO₂and Fe₃O₄distributions. This shows that a Fe₃O₄fine powder is precipitated on a surface of the YSZ.
It is believed that the above result could be obtained by the following reason. Differently from the Fe₃O₄/monoclinic ZrO₂, in the Fe₃O₄/YSZ, a reduced ion is incorporated in a crystal structure of the YSZ during the thermal reduction reaction, instead of being formed as a FeO grain, and then precipitated as a Fe₃O₄grain from the zirconia during the water-decomposition reaction, so that aggregation between FeO grains due to melting/solidification can be avoided.
FIGS. 7(a) to 7(c) show a peak due to the reflection of a Fe₃O₄(311) face in an XRD pattern of the Fe₃O₄(20 wt %)/YSZ during the water-decomposition reaction in each cycle, wherein: FIG. 7(a) shows an XRD pattern before the reaction; FIG. 7(b) shows an XRD 3pattern after the high-temperature thermal reduction reaction at 1400° C.; and FIG. 7(c) shows an XRD pattern after the water-decomposition reaction.
As shown in FIGS. 7(a) and 7(b), in the XRD pattern of the Fe₃O₄/YSZ after the thermal reduction reaction, the peak originated from the Fe₃O₄(311) face becomes weaker than that of the Fe₃O₄/YSZ before the reaction. Further, after the thermal reduction reaction, no peak originated from the FeO is observed in the XRD pattern, and a weak peak of a tetragonal ZrO₂disappears. That is, as seen in FIG. 2(b), in XRD pattern after the thermal reduction reaction, only a strong peak of cubic ZrO₂and a weak peak of Fe₃O₄are observed. Then, after the water-decomposition reaction, as seen in FIG. 7(c), the intensity of a peak originated from Fe₃O₄is increased again.
As evidenced by the above result, during the thermal reduction reaction, the Fe₃O₄reacts with the YSZ through release of oxygen, i.e., Fe⁺²penetrates into a cubic YSZ lattice to form a cubic ZrO₂phase including Fe⁺²or Fe⁺²ion is incorporated in a cubic YSZ lattice, as is commonly known. Then, during the water-decomposition reaction, the Fe⁺²-containing YSZ generates hydrogen through decomposition of water, to form a Fe₃O₄phase on the YSZ support. This cyclical reaction may be roughly represented by the aforementioned formulas (1) and (2). It was also verified that a sample using CSZ has the same reaction mechanism represented by the aforementioned formulas (3) and (4).

TABLE 1

Ferrite Ratio/ Fe₃O₄Conversion Rate/%

wt %-Fe₃O₄ 1st 2nd 3rd 4th 5th 6th 7th

20 27 27 29 29 25 17 25

25 34 18 28 36 33 38 34

TABLE 2


	Temperature
	of Thermal	Hydrogen Generation
Reactive working	Reduction	Amount/Ncm³g⁻¹

material	Reaction/° C.	1st	2nd	3rd	4th	5th	6th	7th

Fe₃O₄	1400	6.9	5.5	7.9	6.6	5.4	6.7	7.8
(20.3 wt %)/YSZ
Fe₃O₄	1400	8.9	4.6	7.1	9.2	8.4	9.9	8.9
(24.5 wt %)/YSZ
Co_0.39Fe_2.61O₄	1400	6.4	2.9	8.3	5.4	8.4	7.5	5.4
(19.5 wt %)/YSZ
CO_0.68Fe_2.32O₄	1400	6.5	5.1	6.0	7.3	6.3	6.2	5.1
(18.3 wt %)/YSZ
Mn_0.68F_2.62O₄	1400	8.0	3.3	5.7	3.4	—	—	—
(16.1 wt %)/YSZ
Fe₃O₄	1400	5.5	6.2	6.7	5.3	5.7	7.2	6.6
(23.4 wt %)/CSZ
CO_0.38Fe_2.62O₄	1400	2.9	3.7	6.5	6.9	5.2	—	—
(18.4 wt %)/CSZ
Fe₃O₄	1400	7.7	7.2	7.4	6.0	4.7	4.2	—
(20.0 wt %)/
monoclinic ZrO₂

INDUSTRIAL APPLICABILITY

The applicant of this patent application previously disclosed an activity of a two-step water-splitting cycle using an iron-based oxide, i.e., ferrite, supported on a zirconia, in Japanese Patent Application No. 2003-060101. Specifically, it was disclosed that the ferrite supported on the zirconia can suppress aggregation and sintering, and thereby allows a two-step water-decomposition reaction to be repeatedly performed in a temperature cycle of 1000° C. and 1400° C. with enhanced reactivity as compared with a ferrite without a zirconia support. It was also disclosed that the occurrence of a phase change between Fe₃O₄and FeO on a surface of the zirconia along with oxidation/reduction reactions of a solid phase is verified using an XRD.
The present invention is based on knowledge that a transition from Fe³⁺to Fe²⁺represented by the aforementioned formulas (1) and (2) or the aforementioned formulas (3) and (4) is observed in a ferrite supported on a cubic zirconia without formation of FeO grain.
In this reaction system, it is believed that Fe²⁺generated through the thermal reduction reaction penetrates into and exists in the cubic zirconia lattice instead of being formed as a FeO crystal, and therefore the melting of the FeO phase is suppressed during the thermal reduction reaction. Thus, in the cubic zirconia-supported ferrite, the melting/aggregation of the FeO phase at 1400° C. can be suppressed.
Further, as compared with a non-stabilized zirconia-supported ferrite, a fully-stabilized or partially stabilized zirconia-supported ferrite is more suitable for a cyclical reaction involving a temperature change in a high-temperature range. The reason is that, while the non-stabilized zirconia is changed from a monoclinic crystal phase to a tetragonal crystal phase due to such a temperature change, iron ions incorporated in the fully-stabilized or partially stabilized zirconia as a solid solution can stabilize a cubic crystal phase thereof to suppress a transition in the crystal phase due to the temperature change. When this zirconia-supported ferrite is fixed onto a ceramic foam to form a reaction device, a junction with the ceramic form is likely to have cracks due to volumetric changes caused by a transition in the crystal phase, and consequently scaling off of the zirconia-supported ferrite. It is expected that the fully-stabilized or partially stabilized zirconia can solve such a problem.

BRIEF DESCRIPTION OF DRAWINGS

FIG. 1 is a schematic diagram showing a high-temperature thermal reduction reactor used in a test on a reactive working material according to the present invention.
FIGS. 2(a) and 2(b) are graphs showing an X-ray diffraction (XRD) pattern in each reaction step.
FIG. 3 is a graph showing a water-decomposition temperature and a hydrogen generation rate per gram of a reactive working material in the I st cycle of a water-decomposition reaction.
FIG. 4 is a graph showing a hydrogen generation amount per gram of the reactive working material in each cycle.
FIGS. 5(a) to 5(d) are scanning electron microscopic (SEM) images of an initial reactive working material and the reactive working material after the 7th cycle.
FIGS. 6(a) to 6(d) are SEM images of a monoclinic zirconia-supported reactive working material.
FIGS. 7(a) to 7(c) are graphs showing changes in Fe₃O₄(311) face based on an XRD pattern in each reaction step

DESCRIPTION OF THE REFERENCE NUMERALS AND SIGNS

1: infrared furnace
2: platinum cup
3: solid sample
4: silica tube
5: R-type thermocouple

Claims

1. A reactive working material for use in a two-step thermochemical water-splitting cycle, said reactive working material comprising a ferrite and a zirconia supporting said ferrite, wherein said ferrite-supporting zirconia is a cubic zirconia.

2. The reactive working material as defined in claim 1, wherein said cubic zirconia contains yttria or calcia in an amount of 2 mol % or more.

3. The reactive working material as defined in claim 1, wherein said ferrite-supporting zirconia is a composite powder of a ferrite fine powder and a zirconia fine powder.

4. The reactive working material as defined in claim 1, wherein said ferrite-supporting zirconia comprises a zirconia porous ceramics body having a porous structure coated with a ferrite fine powder.

5. A method of preparing a reactive working material for use in a two-step thermochemical water-splitting cycle, which comprises a ferrite and a zirconia supporting said ferrite, said method comprising:

dispersing a fully-stabilized or partially-stabilized zirconia fine powder having a particle size of 10 μm or less, in an aqueous Fe (II) salt solution, and adding an aqueous alkali hydroxide solution to said zirconia fine powder-dispersed aqueous solution to form a Fe (II) hydroxide colloid therein;

bubbling air in said colloid-containing aqueous solution to oxidize the Fe (II) hydroxide colloid; and

promoting a dissolution-precipitation reaction where the Fe (II) hydroxide colloid is dissolved in the zirconia fine powder-dispersed aqueous solution and then precipitated as Fe₃O₄, so as to grow Fe₃O₄on the dispersed zirconia fine powder.

6. A method of preparing a reactive working material for use in a two-step thermochemical water-splitting cycle, which comprises a ferrite and a zirconia supporting said ferrite, said method comprising:

dispersing a fully-stabilized or partially-stabilized zirconia fine powder in an aqueous solution of a metal salt of Fe (II);

evaporating and drying the mixture; and

burning the dried mixture to allow the metal salt on the zirconia to be decomposed to the metal oxide; and

heating the metal oxide at a temperature of 300° C. or more.

7. A hydrogen production process based on a two-step thermochemical water-splitting cycle using a reactive working material which comprises a ferrite and an yttria fully-stabilized or partially-stabilized zirconia supporting said ferrite, said process comprising two steps expressed by the following reaction formulas:

x/3Fe₃O₄+Y_yZr_1−yO_2−y/2=Fe_xY_yZr_1−yO_2−y/2+x+x/6O₂; and
Fe_xY_yZr_1−yO_2−y/2+x+x/3H₂O=x/3Fe₃O₄+Y_yZr_1−yO_2−y/2+x/3H₂

8. A hydrogen production process based on a two-step thermochemical water-splitting cycle using a reactive working material which comprises a ferrite and a calcia fully-stabilized or partially-stabilized zirconia supporting said ferrite, said process comprising two steps expressed by the following reaction formulas:

x/3Fe₃O₄+Ca_yZr_1−yO_2−y=Fe_xCa_yZr_1−yO_2−y+x+x/6O₂; and
Fe_xCa_yZr_1−yO_2−y+x+x/3H₂O=x/3Fe₃O₄+Ca_yZr_1−yO_2−y+x/3H₂