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    • 专利摘要:
    Catalytic layer and its use in membranes permeable to oxygen. The present invention relates to a catalytic activation layer for use in oxygen permeable membranes, which may comprise, at least, a porous structure formed by particles of bound ceramic oxides that conduct oxygen ions and electronic carriers, where the surface of said particles exposed to the pores is coated with nanoparticles made of a catalyst whose composition has the following formula: A1-x-ybxcyor Where A may be selected from ti, zr, hf, lanthanide metals and combinations thereof; B and c are metals selected from al, ga, y, sc, b, nb, ta, v, mo, w, re, mn, sn, pr, sm, tb, yb, lu and combinations thereof; A must always be different from b. 0,01 <= x <= 0,5; 0 <= and <= 0.3. (Machine-translation by Google Translate, not legally binding)
    公开号:ES2558183A1
    申请号:ES201430991
    申请日:2014-07-01
    公开日:2016-02-02
    发明作者:Jose Manuel Serra Alfaro；Julio GARCÍA FAYOS；Laura NAVARRETE ALGABA；Vicente Bernardo Vert Belenguer
    申请人:Consejo Superior de Investigaciones Cientificas CSIC；Universidad Politecnica de Valencia；
    IPC主号:
    专利说明:

    Field of the Invention
    The present invention belongs to the field of gas separation membranes. Specifically, it refers to a new catalytic activation layer and its use in an oxygen permeable membrane based on ion-conducting ceramic materials at high temperatures and resistant to operation in the presence of CO2 and other acid gases such as S02. Therefore, its use is mainly oriented to oxy-combustion processes in which a flow enriched in oxidizer (oxygen) is used to obtain high flame temperatures, improve combustion or to avoid N2 contact with process products. An example is the use in oxy-combustion thermal power plants in which combustion gases can be used as entrainment currents in the membrane module. This thermal power plant concept makes it possible to minimize CO2 and NOx emissions.
    State of the art prior to the invention
    Oxy-combustion consists in the use of a high purity O2 stream as a combustion instead of air, as is done in conventional combustion processes, thus reaching higher flame temperatures with lower fuel consumption and thus improving the combustion. The use of oxygen-rich oxidizers makes it possible to obtain combustion gases with a composition consisting mainly of CO2 and water vapor. The high CO2 concentration of the exhaust gases in the oxy-combustion process facilitates the potential separation thereof. In fact, this process of oxy-combustion in thermal or energy-intensive plants makes it possible to produce electrical energy or industrial products from fossil fuels minimizing the emission of CO2, being technologically and economically feasible thanks to its integration with capture technologies and CO2 storage These processes have high energy efficiencies, which allows reducing fuel consumption and reducing the size of industrial units and equipment. Likewise, in the case of combustion only with oxygen instead of air and not feeding N2 to the furnace, reactor or boiler, it is possible to reduce NOx emissions considerably. Therefore, this process has the advantage of facilitating the separation and capture of CO2, which Z 5

    It can be subsequently liquefied, transported and stored or used in other industrial processes. This combustion process concept minimizes CO2 and NOx emissions, as well as substantially increasing the energy efficiency of the process. Examples of energy intensive industries that need the use of oxygen are the glass industry, incinerators, frits manufacturing, enamels and cabbage holes, metallurgy, steel, chemical industry, refining and petrochemicals. One of the industrial sectors in which the use of oxygen makes oxy-combustion possible is that of melting glass and making frits, enamels and ceramic colors. In this type of industries, the need to reach temperatures above 1500 oC inside
    the furnaces, in order to melt the mixture of raw materials that is introduced, is achieved using oxygen instead of air in natural gas burners.
    Essentially, oxy-combustion consists in the combustion of a fuel with oxygen. The oxygen that is fed to the furnace, to the reactor or to the boiler in conditions of high purity, is previously obtained by means of a process of oxygen separation from the air.
    The oxygen membranes can also be applied in the enrichment of the air, so that the oxygen concentration is increased from 21% to higher values, typically above 24%. This increase in concentration is necessary in certain combustion or chemical conversion processes in which the calorific value of the product to be treated, generally a fuel, is insufficient to maintain adequate operating conditions. A typical example of enrichment is the use in cement plants that use alternative fuels or incinerate waste during clinker manufacturing.
    Oxy-combustion aims to be one of the most economical technologies for the capture of CO2, its main drawback being the high demand for O2 and the cost of obtaining it. The great challenge of this technology lies in the production of O2 in order to supply the high quantities that are required.
    Currently, the only technologies available on an industrial scale capable of producing large volumes of O2 are cryogenic distillation of air and absorption facilities in solid absorbent columns (PSA-VPSA), the latter with lower production and generation capacities with lower purities of oxygen, generally less than 95% by volume. The disadvantage of cryogenic air distillation is its high energy consumption. In the case of a thermal power plant, this consumption
    It can amount to 15% of its electricity production, penalizing 10% efficiency
    Global plant. A very interesting alternative and with which it is expected to reduce the loss
    of global efficiency in the oxy-combustion plant up to 5%, is the use of membranes
    dense ceramics based on oxygen ion conductive materials that allow separation
    5 High temperature oxygen with a theoretical purity of 100%.
    The transport of oxygen through the membranes requires temperatures above
    600 ° C to achieve technically competitive permeabilities. The ion transport
    oxygen is simultaneous to the transport of electrons or electronic holes (carriers
    10 electronic), so the material must have sufficient electronic conductivity in the
    membrane operating conditions. The driving force responsible for transport
    of oxygen across the membrane is the difference in partial pressure of oxygen between
    both sides of the membrane. In this way, the flow of oxygen through a membrane
    It is determined by the temperature and the partial pressure difference of the oxygen in addition
    fifteen of the thickness of the membrane.
    Another crucial step in the process of oxygen separation in transport membranes
    Ionic is the gas exchange. As mentioned, transport through the layer
    Selective separation involves the diffusion of oxygen ions and electronic carriers.
    2O Therefore, two super-initial reactions are necessary, a first in which oxygen
    gaseous adsorbs and transforms into oxygen ions in the membrane superstructure
    exposed to feed gases, usually compressed air, and, a second, in the
    that oxygen ions are transformed into molecular oxygen and desorbed. For different
    reasons, these transport stages may be limiting and produce a decrease in
    25 permeation flow through the membrane. Among the different possible reasons, we can
    highlight: (1) the thickness of the selective separation layer is very small, so that the
    diffusion through the solid is much faster than gas exchange. Typically,
    this critical dimension is called "characteristic length" and is the quotient between the
    diffusion coefficient and the kinetic constant of the gas exchange reaction
    30 surface in the operating conditions and composition of gases in contact with the
    membrane surface. (2) Membrane superstition does not possess catalytic activity
    appreciable for the oxygen activation reaction. (3) The gaseous atmospheres in
    contact with the surface or membrane superticies favor the
    adsorption / desorption of molecular oxygen and its evolution through the O2 + 2e · B reaction
    35 0 .2. In industrially relevant processes, both the permeate and the
    Food usually have appreciable amounts of acid gases such as CO2 and S02,

    that hinder such a reaction since they passivate or inactivate the surface and compete with the adsorption and reaction centers involved in the oxygen gas exchange reaction. This pernicious effect is accentuated as the process operating temperature decreases, especially below 850 oC, and when the concentration of 802 and CO2 is increased. Especially negative is the effect of 802 gas, since concentrations above 5 ppm produce severe effects on the permeation of the membrane and in many materials produce irreversible degradations, resulting in the definitive and irreparable damage of the membrane.
    The pressure difference between both sides of the membrane can be achieved through two actions: (a) increasing the air pressure through compression stages; and / or (b) decreasing the partial pressure of oxygen, which is possible by applying vacuum or diluting the oxygen in the permeate by a gaseous stream of entrainment. This last option usually consists of recirculating the exhaust gases of the furnace or combustion boiler, while increasing the operating temperature. Also, in line with the second option, it is possible to pass a reducing gas (generally methane or other hydrocarbons) that consumes the oxygen that permeates through the membrane to give full or partial combustion products and release heat directly in contact with the membrane ceramics.
    Sulfur is present in practically all fuels, in greater or lesser quantity depending on its origin, nature and previous refining and / or purification. Its combustion produces 802 in varying concentrations and in combustion processes that use membranes, it is usually in one way or another in contact with one or both membrane surfaces. Therefore, guaranteeing the stability and effectiveness in the oxygen production of said membranes in atmospheres that contain 802 is a technological aspect to be taken into account for its industrial use.
    Figure 1 shows a scheme of a process that has an oxy-combustion furnace and membrane module in which oxygen is separated from compressed air by applying vacuum in the permeate part. In this process it is necessary to make a contribution of fuel in the compressed air to reach the temperature necessary for the operation of the module. In this process configuration it is necessary for the membrane to function properly in contact with the combustion gases (C02, H20 and 802 mainly) mixed with the air. In other processes, part of the combustion gases of the furnace, boiler or
    reactor as a permeate oxygen entrainment gas and in this case the CO2 concentration,
    H20 and S02 of the gases in contact with the membrane may be larger.
    The selective non-porous separation layer in this type of dense ceramic membranes
    5 It is generally composed of a mixed conductive material of electrons and ions of
    solid-state oxygen with structure of the perovskite family, including in its
    crystal structure alkaline earth elements, rare earths and transition metals such as
    iron and cobalt These oxides have oxygen deficiency in their structure and precisely
    the presence of vacant positions of oxygen in its network makes possible the mechanism of
    10 diffusion of oxygen ion through the crystalline structure. The most used materials
    currently for this application they have crystallized structure of the perovskite type, with
    compositions such as Lao.6Sro.4 Feo.sCo020 J_O or BaOS SrO.5Fe02CoO.SOJ.o. However the
    big problem of this type of materials is its low stability when subjected during
    long periods of time at oxygen concentration gradients and, mainly, at
    fifteen be subject to the presence of CO2 in the operating conditions, producing
    Generally carbonates of alkaline earth elements (carbonation phenomenon). Other
    Type of ionic ceramic membranes are those formed by the mixture of two types of
    crystalline phases, one that predominantly carries oxygen ions and another that
    predominantly transports electrons or electronic holes. For example,
    2 o It has recently been reported that the combination of doped cerium oxide with gadolinium
    with a spinel, free of cobalt and alkaline earth metals, such as Fe2Ni04, has given
    rise to a promising material in terms of its oxygen flow (J. Caro et al., Angewandte
    Ehemie Inlemalional Edilion 2011, 50, 759.)
    25 For practical use, high temperature oxygen separation membranes through
    Ionic transport are generally formed by the following components:
    (i) A porous support, usually made of the same material as it is
    made the separation layer (ii) or a material (ceramic or metallic)
    30 compatible with the separation layer. Compatible means they have a profile
    of similar expansion depending on the temperature and that a
    reaction between both phases at high temperatures to give rise to third phases,
    which generally result in the degradation and breakage of the membrane. The
    Support porosity is usually between 20 and 60%, and its thickness is
    35 It is variable, typically below 2 mm.
    (ii) On the porous support (i) a non-porous layer or film is placed, preferably
    with a thickness of less than 150 I-Im. This layer consists of oxides or
    mixtures of oxides and allows simultaneous transport of oxygen ions and
    electronic carriers through it.
    5 (iii) A porous layer with a thickness is adhered on the non-porous layer (ii)
    preferably between 100 and 10 I-Im, made of a material that has
    mixed ionic and electronic conductivity as well as catalytic activity for the
    adsorption / desorption of oxygen and its dissociation and ionization. This catalytic layer
    It allows to improve the processes of incorporation and elimination of gaseous oxygen.
    10
    Figure 2 shows a diagram of a membrane in which the architecture and
    sequence between (i), (ii) and (iii). The geometry of the membrane in the final module can be
    flat, tubular or any other complex geometry that improves the performance of the
    module, that is, thermofluid dynamics, pressure resistance, heat exchange and
    fifteen proper sealing of the system.
    In some cases, there is an additional porous catalytic layer (iv) between the porous support (i)
    and the non-porous separation layer (ii) which has the function of improving the stages of
    gas exchange, especially when the porous support (i) has no activity
    2O Catalytic does not allow the transport of oxygen ions or electronic carriers.
    Generally, the properties of layer (iii) and layer (iv) are quite similar, if
    Well, generally the specific surface area of the layer (iii) is higher. Figure 3
    shows a diagram of a membrane in which the architecture and sequence is presented
    between (i), (ii), (iii) and (iv).
    25
    Optionally, another additional non-porous layer (v) may also be necessary. This layer is
    it would place between the non-porous layer (ii) and the porous layer (iii), and would serve as protection of the layer
    (ii) against possible interactions or degradation reactions in contact with the layer (iii)
    or with the operating gases in contact with the layer (iii). Layer (v) must allow
    30 transport of oxygen ions and oxygen carriers while being thermo compatible
    chemically with the adjacent layers and with the gases with which it is in contact. The
    Figure 4 shows a diagram of a membrane in which the architecture is presented and
    sequence between (i), (ii), (iii), (iv) and (v).
    Figure 5 shows a scanning electron microscopy image of an oxygen permeable ceramic membrane presenting components (i), (ii) Y (iii), as shown
    5 schematized in Figure 1. Figure 6 shows a scanning electron microscopy image of an oxygen permeable ceramic membrane presenting the components (i), (ii), (iii) Y (v), the latter component being a material composed of two crystalline phases, one that mainly conducts oxygen ions and another that mainly conducts electronic carriers.
    10 15 The present invention relates to a new catalytic activation layer and its incorporation into a catalytically activated oxygen membrane thanks to said catalytic layer that allows efficient operation in the presence of acid gases such as CO2 and 802. Therefore, the present invention provides a solution to improve the performance (permeate flow) of oxygen of a membrane under severe operating conditions, similar to those of oxy-combustion, and therefore overcome the drawbacks of the prior art; also using materials that have a high chemical stability in contact with said gaseous streams. Description of the invention
    2O The present invention relates to a catalytic activation layer for use in oxygen permeable membranes, which may comprise at least one porous structure formed by ceramic oxide particles bonded together that conduct oxygen ions and electronic carriers, where the surface of said particles exposed to the pores is coated with nanoparticles made of a catalyst whose composition has the following formula:
    25
    where
    30 35 A may be selected from Ti, Zr, Hf, lanthanide metals and combinations thereof, preferably Zr, Pr, Ce and combinations thereof; B and e are metals selected from Al, Ga, Y, Sc, B, Nb, Ta, V, Mo, W, Re, Mn, Sn, Pr, Sm, Tb, Yb, Lu and combinations thereof, preferably Al, Ga, Y, Sc, Nb, Mo, W, Pr, 8m and combinations thereof; A must always be different from B. 0.01: S x: s 0.5; O: S Y: S 0.3.
    Said catalytic activation layer may have a thickness preferably between 5 and 100 IJm, a porosity preferably between 10 and 60%, and pores with an average size preferably between 0.1 and 5 IJm, and a catalyst content supported on the porous structure preferably between 0.5 and 10% by weight of said porous structure.
    Likewise, the particles that form the porous structure may have an average grain size, preferably between 0.2 and 5 IJm.
    As an example, the following combinations of metals, Pr-AI and Ce-Pr, have proven to be especially active. Other possible examples would be combinations such as Pr-Ga, Pr-Nb, Pr-W, Pr-Mo, Ce-Al, Ce-Y, Ce-Pr-AI, Cs-Sm-AI, Ce-Sm-Ga, etc. .
    According to a preferred embodiment of the invention, the porous structure may be formed by mixtures of particles having two different crystalline compositions and phases.
    According to a particular embodiment, the porous structure is formed by mixtures of particles that have two different crystalline compositions and phases:
    - a first phase consisting of partially substituted cerium oxide, preferably between 10-30 mol%, by at least one element selected from Zr, Gd, Pr, Sm, Nd, Er, Tb and combinations thereof, preferably Gd , Sm, Tb and combinations thereof, and has a crystalline structure of the florite type, and has an ionic conductivity greater than 0.001 S / cm under operating conditions;
    - a second phase comprising a mixed oxide with a spinel type structure, comprising at least one metal selected from Fe, Ni, Ca, Al, Cr, Mn and combinations thereof, preferably Fe, Ni, Ca, Mn and combinations thereof, and has a total conductivity greater than 0.05 S / cm under operating conditions.
    In another particular embodiment of the invention, the porous structure is formed by mixtures of particles that have two different crystalline compositions and phases:
    35 - a first phase comprising cerium oxide partially substituted (10-30 mol%) by at least one element selected from Zr, Gd, Pr, Sm, Nd, Er, Tb and

    combinations thereof, preferably Gd, Sm, Tb and combinations thereof, and has a crystalline structure of the florite type, and has an ionic conductivity greater than 0.001 S / cm under operating conditions;
    - a second phase comprising a mixed oxide with structure of the perovskite type, comprising at least one metal selected from lanthanides, Fe, Ni, Ca, Cr, Mn and combinations thereof, preferably between Fe, Mn and combinations thereof. themselves, and has a total conductivity greater than 0.05 S / cm under operating conditions.
    The present invention also relates to a process for the preparation of the porous catalytic layer described above. According to a preferred embodiment, the process for obtaining the catalytic activation layer may comprise at least one step of incorporating the catalyst into the surface of the particles of the porous structure by means of a technique selected from impregnation or infiltration of liquid precursor solutions. of the metals included in the final catalyst composition; infiltration of a dispersion of nanoparticles of the catalyst; vapor phase deposition using PVD or CVD techniques and combinations thereof.
    This step of incorporating the catalyst could be carried out in 2 steps, that is, introducing a first element (A), and then, at least, a second element (B) or two more elements (B) and (C) using the techniques described above. It is usual practice to perform a heat treatment after the incorporation of the first element (A) and before the incorporation of another element (B) Doing it in 2 steps can be advantageous in some cases since it can allow to modify or promote preferably the surface of the nanoparticles of the A-based compound without producing any effect within said nanoparticles.
    In addition, according to a particular embodiment, the process for obtaining a catalytic activation layer may further comprise a second stage of heat treatment at temperatures between 650 and 1100 ° C.
    As mentioned above, the catalytic activation layer of the present invention is used in oxygen permeable membranes. Thus, another object of the present invention relates to an oxygen permeable membrane, which comprises said catalytic activation layer. It has been found that with this catalytic activation layer the membrane is especially effective because it substantially improves the stages of
    gas exchange, which totally limit the process of CO2 permeation and especially of gases such as S02. inpresence of
    5 According to a preferred embodiment, the oxygen permeable membrane may comprise at least:
    - a porous (i) ceramic or metal support with a porosity preferably between 20 and 60%, and a thickness preferably less than 2 mm;
    10 - a non-porous layer (ii) with a thickness preferably less than 150 IJm consisting of an oxide or mixtures of oxides that allows simultaneous transport of oxygen ions and electronic carriers therethrough;
    fifteen -a catalytic activation layer (iii) described above. According to a particular embodiment, the membrane may comprise, in addition to the layers described above, the following additional layers:
    2O - an additional porous catalytic layer (iv) between the porous support (i) and the non-porous separation layer (ii) which has the function of improving the stages of gas exchange. Generally, the properties of the layer (iji) and the layer (iv) are quite similar, although generally the specific surface area of the layer (jii) is superior;
    25 30 35 - a non-porous layer (v) q between the non-porous layer (ii) and the porous layer (iii), and would serve as protection of the layer (ii) against possible interactions or degradation reactions in contact with the layer ( iii) or with the operating gases in contact with the layer (iii). The layer (v) must allow the transport of oxygen ions and oxygen carriers while being thermo-chemically compatible with the adjacent layers and with the gases with which it is in contact. According to a preferred embodiment, the catalytic activation layer of the oxygen-permeable membrane may comprise at least one porous structure formed by ceramic oxide particles bonded together that conduct oxygen ions and electronic carriers, where the surface of said particles exposed to the pores is coated with nanoparticles made of a catalyst whose composition has the following formula:
    where
    5 10 A may be selected from Ti, Zr, Hf, lanthanide metals and combinations thereof, preferably Zr, Pr, Ce and combinations thereof; B and e are metals selected from Al, Ga, Y, Sc, B, Nb, Ta, V, Mo, W, Re, Mn, Sn, Pr, Sm, Tb, Yb, Lu and combinations thereof, preferably Al, Ga, Y, Sc, Nb, Mo, W, Pr, Sm and combinations thereof; A must always be different from B. 0.01: S x: S 0.5; °: S Y: S 0.3.
    fifteen In addition, said membrane catalytic activation layer may have a thickness preferably between 5 and 100 µm, a porosity preferably between 10 and 60%, and pores with an average size preferably between 0.1 and 5 µm, and a catalyst content supported on the porous structure preferably between 0.5 and 10% by weight of said porous structure.
    2 o Likewise, the particles that form the porous structure may have an average grain size, preferably between 0.2 and 5 µm.
    25 According to a preferred embodiment of the invention, the porous structure of the catalytic activation layer of the membrane may be formed by mixtures of particles having two different crystalline compositions and phases.
    30 3 5 A particular embodiment would be a membrane whose catalytic activation layer is formed by a porous structure formed by mixtures of particles having two different crystalline compositions and phases: - a first phase consisting of partially substituted cerium oxide, preferably between 10- 30% molar, for at least one element selected from Zr, Gd, Pr, Sm, Nd, Er, Tb and combinations thereof, preferably Gd, Sm, Tb and combinations thereof, and has a crystalline structure of the florite type, and has an ionic conductivity greater than 0.001 S / cm under operating conditions;
    - a second phase comprising a mixed oxide with a spinel type structure, comprising at least one metal selected from Fe, Ni, Ca, Al, Cr, Mn and combinations thereof, preferably Fe, Ni, Ca, Mn and combinations thereof, and has a total conductivity greater than 0.05 S / cm under operating conditions.
    Another particular embodiment would be a membrane whose catalytic activation layer is formed by a porous structure formed by mixtures of particles having two different crystalline compositions and phases:
    10 - a first phase comprising cerium oxide partially substituted (10-30 mol%) with at least one element selected from Zr, Gd, Pr, Sm, Nd, Er, Tb and combinations thereof, preferably Gd, Sm, Tb and combinations thereof, and has a crystalline structure of the florite type, and has an ionic conductivity greater than 0.001 S / cm under operating conditions;
    - a second phase comprising a mixed oxide with structure of the perovskite type, comprising at least one metal selected from lanthanides, Fe, Ni, Co, Cr, Mn and combinations thereof, preferably between Fe, Mn and combinations thereof. themselves, and has a total conductivity greater than 0.05 S / cm under operating conditions.
    The present invention also relates to the process for obtaining the oxygen permeable membrane comprising the catalytic activation layer.
    According to a preferred embodiment, the method of obtaining a membrane
    The oxygen permeable described above and comprising the catalytic activation layer may comprise at least the following steps:
    a) Forming the porous support (i) by a technique selected from uniaxial or isostatic pressing, extrusion or calendering, tape casting (tape casting), conventional casting, immersion coating (dip coating), rotation coating (spin coating) , roller coating or screen printing, physical deposition by sputtering steam, electron beam (electron beam), etc. , spraying of suspensions, and / or thermal spraying, including plasma spraying and spray pyrolysis; 3D printing, stereolithography, injection and combinations of
    35 same.
    b) Forming the non-porous layer (ii) by a technique preferably selected
    between uniaxial or isostatic pressing; extrusion or calendering; tape casting (lape casling),
    conventional casting, dip coating (dip coafing), rotation coating
    (spin coating), roller coating or screen printing; physical deposition by
    5 cathode spray vapor (spuffering), electron beam (electron beam), etc. ,
    atomized; airbrushing; spraying of suspensions; and / or thermal projection
    (thermal spraying), including plasma spray and spray pyrolysis; 3d print,
    Stereolithography, injection, inkjet printing and combinations thereof.
    10 c) Coat the surface of the non-porous separation layer (ii) with a material that
    preferably comprises ceramic oxide particles that conduct oxygen ions and
    electronic carriers using a technique preferably selected from
    nebulized, atomized, thermal or pyrolytic atomized, airbrushing, coating by
    immersion (dip coating), rotation coating (spin coating), roller coating
    fifteen (roller coating), screen printing, chemical or physical vapor deposition technique, (CVO-PVO),
    including sputtering, EB-PVO or PLO, plasma spraying inkjet printing and
    thermal projection, and combinations thereof.
    d) incorporate the catalyst on the surface of the porous structure particles that
    2O cover the non-porous separation layer (ii) by a technique preferably
    selected from impregnation or infiltration of liquid solutions of precursors of the
    metals included in the final catalyst composition; infiltration of a dispersion
    of catalyst nanoparticles; vapor phase deposition using PVO or CVO techniques and
    combinations thereof.
    25 According to a preferred embodiment, the catalyst incorporation step (d) could be
    carry out in 2 steps, that is, enter a first element (A), and then at least one
    second element (B) or two more elements (B) and (C) using the techniques described
    previously.
    30 In addition, according to a particular embodiment of the method of obtaining the membrane,
    this can also comprise a heat treatment stage at temperatures between
    900 and 1250 oC between stages c and d in order to eliminate the organic matter present in the
    layer deposited in (c) and chemically sintering and connecting the ceramic particles between
    Yes and with the underlying non-porous layer.
    35
    P201 430991
    According to another particular embodiment, optionally, a last stage of heat treatment can be carried out at temperatures between 650 and 1100 ° C.
    5 10 According to a particular embodiment, the materials of the porous support (i) may have variable geometry and comprise materials resistant to high temperatures and mechanically and chemically compatible with the materials of the non-porous selective separation layer (ii). Examples of such materials can be, without being limiting: magnesium oxide, aluminum and magnesium spinels, cerium oxide doped with at least one lanthanide metal, zirconium oxide doped with at least one of the following elements Y, Mg, Sc or a lanthanide metal, titanium oxide, aluminum nitride, alloys I refractory superalloys.
    The use of the catalytic activation layer described above for the manufacture of oxygen permeable membranes is likewise object of the present invention.
    fifteen The use of the oxygen permeable membranes described above comprising the catalytic activation layer for the generation of a current rich in O2 is also an object of the present invention.
    2 o These oxygen permeable membranes are especially suitable for generating oxygen fed in oxy-combustion processes and in contact with gases that have CO2 in concentrations greater than 300 ppm and S02 in concentrations greater than 5 ppm.
    25 According to a particular embodiment, the generated O2 stream may have a purity greater than 99% by volume. According to another particular embodiment, the process in which the membrane is used comprises a permeate O2 entrainment gas. This entrainment gas may preferably have an S02 content preferably greater than 5 ppm.
    30 The membrane feed streams that are used are rich in oxygen. A non-limiting example of supply current may be compressed air.
    35 According to a particular embodiment, said supply current has an S02 content greater than 5 ppm.
    According to a preferred embodiment, the described membranes can be used in an integrated manner in an oxy-combustion system or systems comprising oxygen-enriched combustion stages, as described in Figure 1.
    Throughout the description and the claims the word "comprises" and its variants are not intended to exclude other technical characteristics, component additives or steps. For those skilled in the art, other objects, advantages and features of the invention will be derived partly from the description and partly from the practice of the invention. The following examples are provided by way of illustration, and are not intended to be
    Limitations of the present invention.
    Brief description of the figures
    Figure 1. Shows an oxy-combustion system provided with a production unit
    15 of O2 by means of ionic transport membranes. The system uses vacuum in the permeate chamber of the module and different heat exchangers (1), (2) and (3) Figure 2. It shows a simplified representation of a membrane with (i) a porous support, (ii) a layer non-porous selective separation and (iii) a catalytic layer;
    2O Figure 3. It shows a simplified representation of a membrane with (i) a porous support, (iv) an intermediate catalytic layer, (ii) a non-porous layer of selective separation and (iii) an upper catalytic layer; Figure 4. Shows a simplified representation of a membrane with (i) a porous support, (iv) an intermediate catalytic layer, (ii) a non-porous layer of
    Selective separation, (v) a second non-porous separation and protection layer and (iii) a higher catalytic layer; Figure 5. Shows scanning electron microscope image of a cross section of an oxygen permeable ceramic membrane having (i) a porous support, (ii) a non-porous layer of selective separation and (iii) a layer
    30 catalytic;
    Figure 6. Shows scanning electron microscope image of a cross section of an oxygen permeable ceramic membrane having (i) a porous support, (ii) a non-porous layer of selective separation, (v) a second non-porous layer of separation and protection and (iii) a catalytic layer;
    P201 430991
    Examples
    Example 1. A composite material Fe2Ni04-CeoaTbo_20 2.6 (NFO-CTO) is prepared in a 1: 1 volumetric ratio between both crystalline phases by the method called Pechini. 5 This method consists in dissolving the metal precursors, in this almost nitrates, in an aqueous solution containing citric acid in a 2: 1 molar ratio with respect to the metal cations. The water in the solution is evaporated and the resulting residue is calcined at 800 oC in air. NFO-CTO is a composite material that presents mixed conductivity of ions and electronic carriers. The material obtained is used to prepare 10 screen printing inks containing terpineol and ethyl cellulose. Subsequently, two layers of NFO-CTO compound are deposited by screen printing on disks of an ionic conductor (Ce02Gd020 19, CGO), calcined at 1000 oC and porous structures composed of NFO-CTO perfectly adhered to the surface of the CGO disk are obtained. Said disk is obtained by uniaxial commercial powder pressing (Treibacher,
    15 Austria) and later calcined at 1500 oC, and said disk is given a final flat shape by sanding and polishing.
    Example 2. Sample prepared in the same manner as Example A, but to which an aqueous solution of Ce precursors (nitrates) has infiltrated after calcination of the
    20 porous substrate of NFO-CTO. Said infiltration is carried out by adding a certain volume of the precursor solution in each porous layer, so that exactly the added catalyst charge is known. After infiltration, it is calcined at 700 oC so that the catalyst is deposited in its active form.
    Example 3. Sample prepared in the same manner as Example B, but infiltrating on this occasion a nitrate precursor solution of Pr.
    Example 4. Sample prepared in the same way as Example B, but infiltrating this time a nitrate precursor solution of Sm.
    Example 5. Sample prepared in the same way as Example B, but this time infiltrating a precursor solution of Tb nitrate.
    Example 6. Sample prepared in the same way as Example B, but infiltrating on this occasion a precursor solution of nitrate from Co.
    Example 7. Sample prepared in the same way as Example B, but infiltrating this
    occasion a precursor solution of Nb oxalate.
    Example 8. Sample prepared in the same way as Example B, but infiltrating this
    5 occasion an ammonium heptamolybdate precursor solution.
    Example 9. Sample prepared in the same manner as Example B, but this time infiltrating a precursor solution of zirconyl nitrate. Example 10. Sample prepared in the same way as Example B, but infiltrating this
    10 occasion a precursor solution of Al nitrate.
    Example 11. Sample prepared in the same manner as Example C, but adding 20% by volume of the precursor solution considered in Example J to the solution, so that a 80% molar charge of Pr and 20% of Al.
    Example 12. Sample prepared in the same way as Example 8, but adding in this
    20% by volume of the precursor solution considered in Example 8 is added to the solution, so that a 50% molar charge of Pr and 50% Ce is added.
    20 In order to carry out the electrochemical study on each of the materials of the previous examples, an experimental assembly constructed in quartz has been available, capable of withstanding the high temperatures of the study (850 OC).
    Electrochemical characterization by impedance spectroscopy lets you know the
    The effectiveness in the activation of gaseous oxygen, under severe conditions close to its use in oxygen membranes in oxy-combustion processes, of the catalytic layer prepared according to the previous examples. This electrochemical characterization consists in the analysis of the resistive characteristics of the materials by means of the voltammetric impedance spectroscopy method. With this analysis it is possible to characterize the
    30 electrochemical properties under different temperature conditions, and under different atmospheres (in the presence of CO2 and S02).
    To this end, a disk-shaped oxygen ion ceramic material is available on which mixed conductive porous layers of oxygen ions and
    35 electronic carriers with thicknesses around 30 IJm, and on which different catalysts under study have infiltrated. To carry out the measurements, the
    P201 430991
    it shows inside the quartz assembly, connecting current collectors of a highly conductive material in contact with the porous catalytic layers.
    On each side of the ceramic disk, two catalytic porous layers of the reference material are applied by means of a screen printing technique. Subsequently, it is calcined at 1000 oC to consolidate the union of the layers with the disc and so that the porous structure of the support remains stable.
    For each characterization the addition of a catalyst to the porous structure is considered, said addition is made by infiltration of the elements considered from solutions of precursor compounds. Said infiltrations are performed by adding a certain volume to each porous substrate, this being the same for each of the catalysts under study, so that the same material load is always added. Subsequently a calcination of the precursors is carried out, so that the catalysts are infiltrated in their active forms (generally oxides or elementary species).
    The results of the study are shown in Table 1, which shows the polarization resistance in ohms per square centimeter (Q · cm2) obtained for each of the examples at 850 oC after a 10-hour stabilization in each condition in function of the atmospheres to which it has been subjected, including the study in air, CO2 with (5%) O2 and CO2 with (5%) O2 and 250 ppm of S02. The catalytic activity is better the lower the polarization resistance. Although different examples show an improvement with respect to the porous structure without infiltrating (example A) under S02-free conditions, only in three compositions is it possible to obtain a substantial improvement, in some cases, with respect to example A. Such examples, according to the The present invention are those in which the catalyst consists of Ce, but especially those in which two metals were combined in the catalyst, examples K (Pr-AI) and L (Ce-Pr). In the case of the PrAl combination, a metal with high redox catalytic activity was combined under S02-free conditions and a promoter of said activity and which had acidity under operating conditions, and allowed to reduce the adsorption of 802 and its consequent harmful effect on catalytic activity The case of the Ce-Pr combination is similar, Pr was combined with high catalytic activity in air and Ce with more acidity and also relevant catalytic activity. Other possible examples of catalysts following this concept would be combinations such as Pr-Ga, Pr-Nb, Pr-W, Pr-Mo, Ce-Al, Ce-Y, Ce-Pr-AI, Cs-Sm-AI, Ce- Sm-Ga, etc.
    Example 21% O2 in 5% O2 in 5% 02 in 5% O2 in CO2 and 250 ppm (catalyst) N, N, CO, SO,
    A (Not impregnated)B (Ce)C (Pr)D (Sm)E (Tb)F (Co)G (Nb)H (M o)I (Zr)J (Al)K (Pr-AI)L (Pr-Ce)
    1.85 1.10 0.18 0.96 0.52 0.47 5.81 16.69 1.19 2.01 0.22 0.25 2.69 1.31 0.88 1.25 0, 82 0.76 8.91 22.23 1.51 2.82 0.34 0.35 2.71 1.33 1.15 1.31 0.91 0.84 9.47 23.42 1.56 2 , 92 0.35 0.38 7.09 3.83 5.27 6.96 8.70 10.34 12.72 24.11 5.38 9.63 3.33 2.42
    TABLE 1
    Therefore, it has been possible to obtain a high catalytic activity for the activation of gaseous oxygen in oxygen transport membranes in gases containing 250 ppm 5 of 802 using the catalytic layer composed of (1) a porous structure made of a ceramic material having mixed conductivity of oxygen ions and electronic carriers, with adequate porosity and connection between their particles and the underlying membrane and with chemical stability against 802 in the described operating conditions, and (2) a nanoparticle-shaped catalyst dispersed on the surface of the previous porous structure 10 having a composition as described in the preceding paragraph.
    Example 13. An NFO-CTO membrane obtained by uniaxial pressing, screen printing and subsequent calcining at 1400 oC of precursor powder obtained by the Pechini method. Subsequently, a layer of the NFO compound is deposited by screen printing
    5 CTO, calcining at 1000 oC and remaining as a porous structure perfectly adhered to the surface of the non-porous layer. The porous layer obtained is identical to that obtained in example A. The membrane obtained has a porous support (i), a non-porous separation layer of about 100 µm thick (ii) and an upper porous catalytic layer ( iii), according to the scheme shown in Figure 1.
    10 Example 14. Sample prepared in the same manner as described in example M, but to which the solution described in example K has infiltrated both porous substrates. The porous layer obtained is identical to that obtained in example K. The membrane obtained is in accordance with the present invention and has a porous support (i), a non-porous separation layer of about 100 µm thick (ii) and an upper porous catalytic layer (iii), according to the scheme shown in Figure 1.
    fifteen To evaluate the oxygen separation properties of the compounds under study, an experimental assembly constructed in quartz is available in which to analyze the behavior of different ceramic membranes.
    2 or 25 The quartz assembly consists of a tube with two chambers separated by a ceramic membrane, there is no point of communication between the two chambers due to the density (absence of porosity) of the membrane and the sealing performed with O-rings. On the one hand a stream rich in oxygen is fed, while on the other side a entrainment gas is circulated or the vacuum is induced. This difference in oxygen content conditions serves as a driving force for the diffusion of oxygen from the feed-rejection side to the permeate side. Quantifying the oxygen content in the permeate stream by means of a gas chromatograph determines the flow of oxygen that permeates through the membrane under different temperature conditions, oxygen content in the feed chamber and aggressive atmospheres in the permeate (presence of CO2 and S02).
    30 35 Oxygen permeation was studied in membranes according to examples M and N. Permeation assays and catalytic studies were carried out in disc-shaped membranes of diameter 15 mm and approximately 1 mm thick. The reaction temperature is controlled by a thermocouple near the membrane. The permeate gas stream was analyzed using a Varian CP-4900 micro-CG equipped with three analysis modules: Molsieve5A, PoraPlot-Q and CP-Sil. Table 2 shows the permeation of oxygen obtained in milliliters (normal conditions) per minute and
    square centimeter (Nml '' min, 1'cm, 2) for membranes according to examples M and N in different atmospheres at 730 oC after a stabilization of 8 hours in each condition. The results show that the membrane according to the present invention (example N) has a much greater oxygen permeation than the membrane (example M) without
    5 catalyst infiltrated in layer (iii). The difference between both membranes is much moreimportant when the permeate contains S02, conditions in which it is difficultnotably the gaseous exchange of oxygen and, therefore, the effect of a catalystActive becomes much more important.
    10 Table 2
    Example (catalyst) Trailed gas Trailed gas Trailed gasAr 100% CO2 100% CO, and 250 ppm SO,
    M (Not impregnated) 0.8 0.6 0.1 N (Pr-AI) 1.6 1.3 1.0
    权利要求:
    Claims (12)
    [1]
     Claims

    5 1. A catalytic activation layer for use in oxygen permeable membranes, characterized in that it comprises, at least, a porous structure formed by ceramic oxide particles bonded together that conduct oxygen ions and electronic carriers, coated with nanoparticles made of a catalyst whose composition has the following formula:
    10 where
    fifteen A is selected from Ti, Zr, Hf, lanthanide metals and combinations thereof; S and c are metals selected from Al, Ga, Y, Se, S, Nb, Ta, V, Mo, W, Re, Mn, Sn, Pr, Sm, Tb, Yb, Lu and combinations thereof; A must always be different from S; 0.01 s x s 0.5; ° s and s 0.3.
    2 o and has a thickness between 5 and 100 µm, a porosity between 10 and 60%, and pores with an average size between 0.1 and 5 µm, and a catalyst content supported on the porous structure between 0, 5 and 10% by weight of the porous structure.
    25 30 35 2. A catalytic activation layer according to claim 1, characterized in that the porous structure is formed by mixtures of particles having two different crystalline compositions and phases: - a first phase consisting of cerium oxide partially substituted by a selected element between Zr, Gd, Pr, Sm, Nd, Er, Tb and combinations thereof, and has a crystalline structure of the florite type, and has an ionic conductivity greater than 0.001 S / cm under operating conditions; - a second phase comprising a mixed oxide with a spinel type structure, comprising at least one metal selected from Fe, Ni, Co, Al, Cr, Mn and combinations thereof and having a total conductivity greater than 0, 05 S / cm under operating conditions.
    [3]
    3. A catalytic activation layer according to claim 1, characterized in that the
    porous structure, is formed by mixtures of particles that have two compositions and
    different crystalline phases:
    - a first phase comprising cerium oxide partially replaced by a
    5 element selected from Zr, Gd, Pr, Sm, Nd, Er, Tb and combinations thereof, and
    It has a crystalline structure of the florite type, and has an ionic conductivity greater than 0.001
    S / cm under operating conditions;
    -a second phase comprising a mixed oxide with structure of the perovskite type,
    comprising at least one metal selected from lanthanides, Fe, Ni, Ca, Cr, Mn and
    10 combinations thereof and has a total conductivity greater than 0.05 S / cm in
    Operating conditions.
    [4]
    4. Procedure for obtaining a catalytic activation layer described in the
    claims 1 to 3, characterized in that it comprises at least one stage of
    fifteen incorporation of the catalyst on the surface of the porous structure particles
    by a technique selected from impregnation or infiltration of liquid solutions
    of precursors of metals comprised in the final catalyst composition;
    infiltration of a dispersion of nanoparticles of the catalyst; vapor deposition
    by means of PVO or evo techniques and combinations thereof.
    twenty
    [5]
    5. Procedure for obtaining a catalytic activation layer according to claim 4,
    characterized in that it also comprises a second stage of heat treatment a
    temperatures between 650 and 1100 oC.
    25 6. An oxygen permeable membrane, characterized in that it comprises at least:
    -a porous (i) ceramic or metallic support with a porosity between 20 and 60%, and a thickness
    lower 2 mm;
    - a non-porous layer (ii) with a thickness of less than 150 iJm consisting of an oxide or
    mixtures of oxides that allow simultaneous transport of oxygen ions and carriers
    3O electronic through;
    -a catalytic activation layer (iii), described in claims 1 to 3 and obtained
    according to the procedure described in claims 4 and 5.
    [7]
    7. Procedure for obtaining an oxygen permeable membrane described in the
    35 claim 6, characterized in that it comprises at least the following steps:
    a) Forming the porous support (i) by a technique selected from uniaxial or isostatic pressing, extrusion or calendering, tape casting, conventional casting, immersion coating, rotation coating, roller or screen printing, physical vapor deposition, fogging of suspensions, and / or thermal projection, 3D printing,
    5 stereolithography, injection and combinations thereof.
    b) Forming of the non-porous layer (ii) by a technique selected from uniaxial or isostatic pressing; extrusion or calendering; tape casting, conventional casting, dip coating, rotation coating, roller coating or
    10 screen printing; physical vapor deposition, suspension nebulization; and / or thermal projection, 3D printing, stereolithography, injection, inkjet printing and combinations thereof.
    c) Coat the surface of the non-porous separation layer (ii) with a material that
    15 comprises ceramic oxide particles that conduct oxygen ions and electronic carriers by a technique selected from fogging, atomizing, thermal or pyrolytic atomization, airbrushing, immersion coating, rotation coating, roller coating, screen printing, chemical or physical deposition technique in vapor phase, inkjet printing and thermal projection, and combinations thereof.
    D) incorporating the catalyst into the surface of the particles of the porous structure that covers the non-porous separation layer (ii) by a technique selected from impregnation or infiltration of liquid solutions of metal precursors comprised in the final catalyst composition ; infiltration of a dispersion of
    25 catalyst nanoparticles; vapor phase deposition using PVO or evo techniques and combinations thereof.
    [8]
    8. Procedure for obtaining an oxygen permeable membrane according to the
    claim 7, characterized in that it further comprises a thermal treatment stage 30 at temperatures between 900 and 1250 ° C between stages c and d.
    [9]
    9. Method of obtaining an oxygen permeable membrane according to claims 7 and 8, characterized in that it also comprises a final stage of heat treatment at temperatures between 650 and 1100 oC.
    [10]
    10. Use of a catalytic activation layer, described according to claims 1 to 3 and obtained according to the process described in claims 4 and 5, for the manufacture of oxygen permeable membranes.
    5 11. Use of a membrane described in claim 6 and obtained according to the methoddescribed in claims 7 to 9, for the generation of a current rich in O2.
    [12]
    12. Use of a membrane according to claim 11, characterized in that the generated O2 current has a purity greater than 99% by volume.
    [13]
    13. Use of a membrane according to claim 11, characterized in that it comprises a permeate O2 entrainment gas.
    [14]
    14. Use of a membrane according to claim 13, characterized in that the entrainment gas has a content of 802 greater than 5 ppm.
    [15]
    15. Use of a membrane according to claims 11 to 14, characterized in that the membrane feed current has a content of 802 greater than 5 ppm.
    16. Use of a membrane according to claims 11 to 15, integrated in an oxy-combustion system or systems comprising oxygen-enriched combustion stages.
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    同族专利:
    公开号 | 公开日
    EP3165278A1|2017-05-10|
    US20170100697A1|2017-04-13|
    EP3165278A4|2018-02-14|
    WO2016001465A1|2016-01-07|
    US10213735B2|2019-02-26|
    ES2558183B1|2016-11-11|
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