Patent Application
20220178035
The present disclosure relates to an anti-corrosive, electrically conductive magnesium titanium oxide material with oxygen vacancies.
Metals have been a widely used material for thousands of years. Various methods have been developed to preserve metals and prevent their corrosion or disintegration into oxides, hydroxides, sulfates, and other salts. Metals in some industrial applications are especially susceptible to corrosion due to aggressive operating environments. Non-limiting examples may be metal components of an electrochemical cell such as a fuel cell bipolar plate (BPP) or a fuel cell or electrolyzer catalyst support material. In addition, certain components such as the BPP are required to not only be sufficiency chemically inert to resist degradation in the highly corrosive environment of the fuel cell, but also be electrically conducting to facilitate electron transfer for the oxygen reduction reaction of the fuel cell. Finding a material that meets both the requirements has been a challenge.
According to a non-limiting embodiment, an electrolyzer system is disclosed. The electrolyzer system includes an anticorrosive, conductive material including a first oxide having oxygen vacancies and a formula (Ia):
MgTi2Os5-δ (Ia),
where δ is any number between 0 and 3 including a fractional part denoting the oxygen vacancies. The material also includes a second oxide having a formula (II):
TiaOb (II),
where 1<=a<=20 and 1<=b<=30, optionally including a fractional part. The first and second oxides of formulas (Ia) and (II) may form a polycrystalline matrix within the electrolyzer system. The polycrystalline matrix may be porous. The porous polycrystalline matrix may be structured as a catalyst support. The Mg/Ti ratio may be about 0.01-0.8. The system may include a porous transport layer (PTL) including the anticorrosive, conductive material. The polycrystalline matrix may include nanofibers with a diameter of about 10 to 250 nm. TiaOb may be Ti2O3. The system may include a bipolar plate including the polycrystalline matrix.
In an alternative embodiment, an electrochemical cell material is disclosed. The electrochemical cell material may include an anticorrosive, conductive polycrystalline matrix having: a first metal oxide having oxygen vacancies and a formula (Ib):
Mg1−xTi2+xO5-δ (Ib),
where δ is any number between 0 and 3 including a fractional part denoting the oxygen vacancies, and 0<=x<=1.
The anticorrosive, conductive polycrystalline matrix may include a second metal oxide having a formula (II):
TiaOb (II),
where 1<=a<=20 and 1<=b<=30, optionally including a fractional part. The first and second oxides may form a polycrystalline matrix. The material may be a porous microfiber. The matrix may include sintered fibers. The fractional part in a, b, or both may be included. The matrix may form a surface layer of a component in the electrochemical cell. The electrochemical cell may be an electrolyzer.
In yet another embodiment, an electrochemical cell component is disclosed. The electrochemical cell includes an anticorrosive, conductive, nonstoichiometric material having a first metal oxide having oxygen vacancies and a formula (Ib):
Mg1−xTi2+xO5-δ (Ib),
where δ is any number between 0 and 3 including a fractional part denoting the oxygen vacancies, and 0<=x<=1. The Mg/Ti ratio in the material of the formula (Ib) may be about 0.01 to about 0.8. The component may be a bipolar plate. The component may be a porous transport layer material. The electrochemical cell may be an electrolyzer. The material may have excess Ti such that 0<x<=1. The component may be a catalyst support.
Embodiments of the present disclosure are described herein. It is to be understood, however, that the disclosed embodiments are merely examples and other embodiments may take various and alternative forms. The figures are not necessarily to scale; some features could be exaggerated or minimized to show details of particular components. Therefore, specific structural and functional details disclosed herein are not to be interpreted as limiting, but merely as a representative basis for teaching one skilled in the art to variously employ the present embodiments. As those of ordinary skill in the art will understand, various features illustrated and described with reference to any one of the figures may be combined with features illustrated in one or more other figures to produce embodiments that are not explicitly illustrated or described. The combinations of features illustrated provide representative embodiments for typical applications. Various combinations and modifications of the features consistent with the teachings of this disclosure, however, could be desired for particular applications or implementations.
Except where expressly indicated, all numerical quantities in this description indicating dimensions or material properties are to be understood as modified by the word “about” in describing the broadest scope of the present disclosure.
The first definition of an acronym or other abbreviation applies to all subsequent uses herein of the same abbreviation and applies mutatis mutandis to normal grammatical variations of the initially defined abbreviation. Unless expressly stated to the contrary, measurement of a property is determined by the same technique as previously or later referenced for the same property.
The term “substantially” or “about” may be used herein to describe disclosed or claimed embodiments. The term “substantially” or “about” may modify a value or relative characteristic disclosed or claimed in the present disclosure. In such instances, “substantially” or “about” may signify that the value or relative characteristic it modifies is within ±0%, 0.1%, 0.5%, 1%, 2%, 3%, 4%, 5%, or 10% of the value or relative characteristic.
The description of a group or class of materials as suitable for a given purpose in connection with one or more embodiments implies that mixtures of any two or more of the members of the group or class are suitable. Description of constituents in chemical terms refers to the constituents at the time of addition to any combination specified in the description, and does not necessarily preclude chemical interactions among constituents of the mixture once mixed. First definition of an acronym or other abbreviation applies to all subsequent uses herein of the same abbreviation and applies mutatis mutandis to normal grammatical variations of the initially defined abbreviation. Unless expressly stated to the contrary, measurement of a property is determined by the same technique as previously or later referenced for the same property.
Metals present a widely used group of materials in numerous industries including automotive, construction, home appliances, tools, pipes, railroad tracks, coinage, etc. Metals have been utilized for thousands of years and have remained a material of choice for certain applications due to their properties such as strength and resilience. Yet, corrosion of metals is a major source of fatigue and lifetime limitations for a number of applications using metals.
Corrosion is a natural process which converts a refined metal to a more chemically-stable form such as the metal's oxide(s), hydroxide(s), sulfide(s), and/or other salts. The conversion presents a gradual destruction of the metal material caused by electrochemical oxidation of the metal in a reaction with an oxidant such as oxygen or sulfates. Corrosion may be invoked by exposure of the metal substrate to moisture in the air, to a solution with a relatively low pH, various chemical substances such as acids, microbes, elevated temperatures, and/or other factors. Especially in acidic environments, corrosion starts at the interface between a bulk metal material (e.g., steel) and a solution (e.g., ions dissolved in water or water surface layer which react to degrade the bulk material).
Many efforts have been made to prevent or slow down corrosion of metals. For instance, various types of coatings have been developed. Example coatings include applied coatings such as paint, plating, enamel; reactive coatings including corrosion inhibitors such as chromates, phosphates, conducting polymers, surfactant-like chemicals designed to suppress electrochemical reactions between the environment and the metal substrate, anodized surfaces, or biofilm coatings. Other methods of corrosion prevention include controlled permeability framework, cathodic protection, or anodic protection.
Yet the most popular solution to the corrosion problem remains to be fortifying of the vulnerable metal surface with a coating. Most corrosion-resistant surfaces thus include one or more chemically inert coatings or protective layers that can slow down and/or at least partially prevent corrosion from occurring. Still, it has remained a challenge to find a material with substantial anticorrosion properties which would be also friendly to the environment, economical, while having superb performance characteristics.
Moreover, some applications are highly susceptible to corrosion due to their environmental factors. A non-limiting example of such application are proton-exchange-membrane fuel cells (PEMFC). The PEMFC represents an environmental-friendly alternative to internal combustion engines for a variety of vehicles such as cars and buses. The PEMFC typically features a relatively high efficiency and power density. A very attractive feature of the PEMFC engine are no carbon emissions, provided that the hydrogen fuel has been gained in an environmentally-friendly manner. Besides being a green engine, the PEMFC may be used in other applications such as stationary and portable power sources.
The PEMFC's own operating environment lends itself to corrosion for a variety of reasons. For example, low voltages exist between startups and shutdowns of the PEMFC, PEMFC has a strongly acidic environment, fluorine ions are released from the polymer membrane during operation of the PEMFC, both H2 and O2 exist at the anode during the startup and shutdown which causes high cathodic potential yielding cathodic corrosion, fuel crossover of hydrogen or oxygen from the anode to cathode or vice versa, etc. The PEMFC thus requires durable components capable of withstanding the above-mentioned conditions.
A non-limiting example of a PEMFC is depicted in
The bipolar plates or BPP 20 are implemented in a PEMFC stack to distribute gas, collect current, and separate individual cells in the stack from each other. The BPP 20 also provides additional functions such as removal of reaction products and water as well as thermal management within the PEMFC 10. The BPP 20 is also a relatively expensive component and a frequent reason for degradation of the PEMFC system. For example, BPPs may constitute about 60-80% of the stack weight, about 50% of the stack volume, and about 25-45% of the stack cost. To keep the cost low, the BPP 20 is typically made from metal, for example steel such as stainless steel. Alternative materials such as aluminum or titanium may be used. As the metal plates are susceptible to corrosion within the PEMFC system, efforts have been made to prevent the corrosion.
Additionally, in the PEMFC 10, the BPP 20 presents yet another material challenge as the BPP 20 is also required to be electrically conducting to facilitate electron transfer for the oxygen reduction reaction. Therefore, the BPP 20 material needs to be electrically conducting but chemically inert to reactions with ions present in the PEMFC 10 environment.
Typically, the BPP metal surface contains a coating such as graphite-like coating or protective oxide or nitride coatings to increase corrosion resistance of the BPP 20. The BPP's 20 surface may thus include elements such as Fe, Cr, Ni, Mo, Mn, Si, P, C, S, F, or a combination thereof. Alternative coatings include Ti alloy, doped TiO %, Cr2O3, TiO2, TiN, CrN, or ZrN. Yet, in an aggressively corrosive environment such as in the PEMFC 10, where coatings are more likely to degrade faster than in other applications, a need remains for a coating or material that would be economically feasible, corrosion resistant, protective against acids such as HF at PEMFC operating temperature of about 80° C., electrically conductive, and capable of forming a coherent interface (i.e., a small interfacial contact resistance) with the metal substrates at the same time.
Besides fuel cells, electrolyzers present another type of an electrochemical cell. Electrolyzers use electrical energy to conduct chemical reactions. Electrolyzers undergo an electrolysis process to split water into hydrogen and oxygen, providing a promising method for hydrogen generation from renewable resources. An electrolyzer, like a fuel cell, includes an anode and cathode catalyst layers separated by an electrolyte membrane. The electrolyte membrane may be a polymer, an alkaline solution, or a solid ceramic material. A catalyst material is included in the anode and cathode catalyst layers of the electrolyzer.
Electrolyzers are being used for hydrogen production from water. However, widespread adoption of the electrolyzer cells requires further research into lifetime and cost reduction for components used in these electrochemical cells. The electrolyzer components include an electrolyte membrane and catalyst layers separated by the electrolyte membrane.
A typical single electrolyzer is composed of an electrolyte membrane, an anode layer, and a cathode layer separated from the anode layer by the electrolyte membrane. A non-limiting schematic depiction of an electrolyzer 30 is shown in
A catalyst material, such as Pt-based catalysts, is included in the anode and cathode layers 34, 36 of the electrolyzer 30. At the anode layers 34, H2O is hydrolyzed to O2 and H+ (2H2O→O2+4 H+4e−). At the cathode layers 36, H+ combines with electrons to form H2 (4H++4e−→2H2).
A depiction of the electrolysis principal, utilized by a proton exchange membrane (PEM) electrolyzer 30, with relevant reactions is depicted in
During electrolysis, water is broken down into oxygen and hydrogen in anodic and cathodic electrically driven evolution reactions. The reactant liquid water (H2O) permeates through the anode 34 PTL to the anode catalyst layer, where the oxygen evolution reaction (OER) occurs. The protons (H+) travel via the PEM 32, and electrons (e−) conduct through an external circuit during the hydrogen evolution reaction (HER) at the cathode 36 catalyst layer. The anodic OER requires a much higher overpotential than the cathodic HER. It is the anodic OER which determines efficiency of the water splitting due to the sluggish nature of its four-electron transfer.
The PTL allows transport of electrons from catalyst layer to the bipolar plate. At the same time, PTL should allow the gas transport produced from the electrode, as well as water transport toward the electrode. Similar to other PEM electrolyzer components, the PTL needs to have good electrical conductivity and corrosion resistance at high voltage operation. Other design criteria include: porosity, mechanical stability, resistance against H embrittlement, low contact resistance (next to catalyst layer and BPP), etc.
Various materials are used to produce the PEM electrolyzer or PEME 30. Similar to PEMFC, the bipolar plate (BPP) accounts for significant cost among PEME components. In fact, a PEME BPP is typically more expensive than a PEMFC BPP due to usage of Ti metal (or other metals that are more stable against corrosion). The PEME BPP also needs to have a good chemical resistance on the anode side (against O2) and the cathode side (against H embrittlement and oxidation). In commercial PEME stacks, the anode side additionally requires a coating layer if the metal used is a different metal than Ti. Alternative bulk metal includes stainless steel, copper, or aluminum-based alloy systems. Previously, Au, Ti, TiN, TiN/C, TaN, and F-doped tin oxide (FTO) have been explored as chemically resistant BPP coating materials in a PEME BPP.
In an electrolyzer, the local environment is more corrosive and severe for the PTL on the anode side than on the cathode side. Therefore, more corrosion resistant materials and structures are typically incorporated for the anode PTL than for the cathode PTL. An example of the anode PTL layer material may be titanium (Ti) or Pt. For the PTL on the cathode side, similar type of technology as in PEMFC may be adapted. Thus, the cathode PTL layer may include carbon-based materials such as carbon paper, carbon fleece, etc. The PEM 32, anode 34, and cathode 36 may be surrounded by the BPPs which may be made, for example, from Ti or gold- or platinum-coated Ti metals.
The catalysts are typically used on the anode side 34 and the cathode side 36 to assist with the half-reaction processes. The typical catalyst material on the cathode 36 is platinum (Pt) while the typical catalyst used on the anode 34 is ruthenium (Ru), iridium (Ir), Ir—Ru, ruthenium oxide (RuO2), iridium oxide (IrO2), or iridium-ruthenium oxide (Ir—Ru—O) due to a combination of a relatively high activity and durability. But large-scale use and production of PEM electrolyzes, and fuel cells utilizing PEM electrolyzes, requires substantial amount of the catalyst materials which poses a problem for the industry. Out of all PEME components, the anode catalyst is the most expensive constituent due to use of the rare metals Ir and/or Ru and lack of opportunity to reduce its cost through economies-of-scale effects.
At the anode 34, Ir typically catalyzes the EOR (H2O→2H+½O2+2e−); and, at the cathode 36, Pt typically catalyzes the HER (2H++2e−→H2). The cell temperature typically ranges from about 50 to about 80° C. The cell voltage in the electrolyzer 30 is rather high compared to a fuel cell (greater than 1.23 V), typically ranging from 1.8 to 2.2 V vs. SHE at full load. Due to relatively high operating voltage, the electrolyzer 30 materials may undergo further catalyst degradation (e.g., metal dissolution that may lead to the loss in electrochemically active surface area), which may affect the entire electrolyzer stack system 40 throughout its lifetime.
Anode catalyst materials such as Ir/Ru/IrOx/RuOx, etc. may be dispersed on chemically stable supports in PEME. While carbon-based support is acceptable and widely used in PEMFC and PEME cathodes, PEME anodes typically need to operate at even higher voltage for carrying out OER reactions. In the highly oxidizing environment of PEME, corrosion of the support materials could potentially lead to a breakdown of catalyst layer porous structure. This could decrease the electrical conduction and decrease the water management efficiency in a PEME stack. Therefore, metal oxides may be used instead of carbon-based materials in PEME anodes. For example, TiOx, NbOx, SnOx, and other doped metal oxides have been investigated as possible support materials for OER catalysts. While these materials help improve the mass activity of OER catalysts at initial conditions, their long-term durability has been a drawback due to a loss in conductivity.
The material disclosed herein solves one or more problems described above and/or provides the benefits identified herein. It was surprisingly discovered that the disclosed material provides anticorrosive, conductive properties to a substrate. The substrate may include, but not be limited to an electrochemical cell substrate, a PEMF substrate, a PEME substrate, a PEMF catalyst support, a PEMF BPP substrate, a PEME BPP metal substrate, a PEME catalyst support, or a PEME PTL. Other types of substrates are contemplated and discussed below.
The material encompasses a first oxide material including a variety or a series of Mg—Ti compounds with different contents of oxygen vacancies or, in other words, Mg—Ti compounds with a variety of oxygen-deficient stoichiometries, a second oxide material, or both.
A non-limiting example of a BPP 20 is shown in
The surface portion 24 may include the anticorrosive, chemically inert, electrically conductive, and thermodynamically stable material disclosed herein. The entire area of the surface portion 24 may include the material. Alternatively, the surface portion 24 may include one or more subportions which are free from the material. In an example embodiment, the entire surface portion 24 may include the material such that the entire BPP 20 is protected against corrosion. In other applications such as non-BPP applications, only a small portion of the surface portion 24 may include the material such as less than about ½, ¼, ⅛, 1/16, 1/32, or the like of the surface portion may include the material.
The surface portion 24, the bulk portion 22, or both may include one or more layers of the disclosed material. The material thickness on the surface portion 24 may be adjusted according to the needs of a specific application. A non-limiting example of the material layer thickness may be about 0.1 to 0.8 μm, 0.2 to 0.6 μm, or 0.3 to 0.5 μm. Alternatively, the material may be layered to form a relatively thick deposit with dimensions of more than 1 μm on the surface portion 24 such as about or at least about 1.25, 1.5, 1.75, 2.0, 2.25, 2.5, 2.75, 3.0, 3.25, 3.5, 3.75, 4.0, 4.25, 4.5, 4.75, 5.0, 10, 15, 20, 25, 30, 35, 40, 45, 50, 55, 60, 65, 70, 75, 80, 85, 90, 95, 100, 110, 120, 130 140, 150, 200, 250 μm or about 1.25, 1.5, 1.75, 2.0, 2.25, 2.5, 2.75, 3.0, 3.25, 3.5, 3.75, 4.0, 4.25, 4.5, 4.75, 5.0, 10, 15, 20, 25, 30, 35, 40, 45, 50, 55, 60, 65, 70, 75, 80, 85, 90, 95, 100, 110, 120, 130 140, 150, 200, 250, 300, 350, 400, 450, or 500 nm. The material may form one or more layers or a plurality of layers on the bulk portion 22. The material may form 1, 2, 3, 4, 5, 6, 7, 8, 9, 10, or more layers on the bulk portion 22. Each layer may have a thickness within the nanoscale or microscale recited herein with respect to the thickness of the surface portion 24.
The disclosed material includes a first oxide Mg—Ti—O-based material. The disclosed material may have a formula (Ia), formula (Ib), or both:
MgTi2O5-δ (Ia),
Mg1−xTi2+xO5-δ (Ib),
where
0<=x<=1 such that x may be any number between and including 0 and 1. x may be 0.01, 0.02, 0.03, 0.04, 0.05, 0.06, 0.07, 0.08, 0.09, 0.10, 0.11, 0.12, 0.13, 0.14, 0.15, 0.16, 0.17, 0.18, 0.19, 0.20, 0.21, 0.22, 0.23, 0.24, 0.25, 0.26, 0.27, 0.28, 0.29, 0.30, 0.31, 0.32, 0.33, 0.34, 0.35, 0.36, 0.37, 0.38, 0.39, 0.40, 0.41, 0.42, 0.43, 0.44, 0.45, 0.46, 0.47, 0.48, 0.49, 0.50, 0.51, 0.52, 0.53, 0.54, 0.55, 0.56, 0.57, 0.58, 0.59, 0.60, 0.61, 0.62, 0.63, 0.64, 0.65, 0.66, 0.67, 0.68, 0.69, 0.70, 0.71, 0.72, 0.73, 0.74, 0.75, 0.76, 0.77, 0.78, 0.79, 0.80, 0.81, 0.82, 0.83, 0.84, 0.85, 0.86, 0.87, 0.88, 0.89, 0.90, 0.91, 0.92, 0.93, 0.94, 0.95, 0.96, 0.97, 0.98, 0.99, 1.0. x may be greater than 0 and lower than 1 such that 0<x<1. The formula (Ib) may have excess Ti such that 0<x<=1. 0<=x<1 is likewise contemplated.
In formulas (Ia) and (Ib), δ is any number between 0 and 3, optionally including a fractional part such as decimals and/or hundredths and denotes oxygen vacancies. S may be 0.1, 0.2, 0.3, 0.4, 0.5, 0.6, 0.7, 0.8, 0.9, 1.0, 1.1, 1.2, 1.3, 1.4, 1.5, 1.6, 1.7, 1.8, 1.9, 2.0, 2.1, 2.2, 2.3, 2.4, 2.5, 2.6, 2.7, 2.8, 2.9, or 3.0. δ may be any number between 0 and 3 including tenths, hundredths, or both. 6 may be 0.01, 0.02, 0.03, 0.04, 0.05, 0.06, 0.07, 0.08, 0.09, 0.10, 0.11, 0.12, 0.13, 0.14, 0.15, 0.16, 0.17, 0.18, 0.19, 0.20, 0.21, 0.22, 0.23, 0.24, 0.25, 0.26, 0.27, 0.28, 0.29, 0.30, 0.31, 0.32, 0.33, 0.34, 0.35, 0.36, 0.37, 0.38, 0.39, 0.40, 0.41, 0.42, 0.43, 0.44, 0.45, 0.46, 0.47, 0.48, 0.49, 0.50, 0.51, 0.52, 0.53, 0.54, 0.55, 0.56, 0.57, 0.58, 0.59, 0.60, 0.61, 0.62, 0.63, 0.64, 0.65, 0.66, 0.67, 0.68, 0.69, 0.70, 0.71, 0.72, 0.73, 0.74, 0.75, 0.76, 0.77, 0.78, 0.79, 0.80, 0.81, 0.82, 0.83, 0.84, 0.85, 0.86, 0.87, 0.88, 0.89, 0.90, 0.91, 0.92, 0.93, 0.94, 0.95, 0.96, 0.97, 0.98, 0.99, 1.0, 1.01, 1.02, 1.03, 1.04, 1.05, 1.06, 1.07, 1.08, 1.09, 1.1, 1.11, 1.12, 1.13, 1.14, 1.15, 1.16, 1.17, 1.18, 1.19, 1.20, 1.21, 1.22, 1.23, 1.24, 1.25, 1.26, 1.27, 1.28, 1.29, 1.30, 1.31, 1.32, 1.33, 1.34, 1.35, 1.36, 1.37, 1.38, 1.39, 1.40, 1.41, 1.42, 1.43, 1.44, 1.45, 1.46, 1.47, 1.48, 1.49, 1.50, 1.51, 1.52, 1.53, 1.54, 1.55, 1.56, 1.57, 1.58, 1.59, 1.60, 1.61, 1.62, 1.63, 1.64, 1.65, 1.66, 1.67, 1.68, 1.69, 1.70, 1.71, 1.72, 1.73, 1.74, 1.75, 1.76, 1.77, 1.78, 1.79, 1.80, 1.81, 1.82, 1.83, 1.84, 1.85, 1.86, 1.87, 1.88, 1.89, 1.90, 1.91, 1.92, 1.93, 1.94, 1.95, 1.96, 1.97, 1.98, 1.99, 2.0, 2.01, 2.02, 2.03, 2.04, 2.05, 2.06, 2.07, 2.08, 2.09, 2.1, 2.11, 2.12, 2.13, 2.14, 2.15, 2.16, 2.17, 2.18, 2.19, 2.20, 2.21, 2.22, 2.23, 2.24, 2.25, 2.26, 2.27, 2.28, 2.29, 0.30, 2.31, 2.32, 2.33, 2.34, 2.35, 2.36, 2.37, 2.38, 2.39, 2.40, 2.41, 2.42, 2.43, 2.44, 2.45, 2.46, 2.47, 0.48, 2.49, 2.50, 2.51, 2.52, 2.53, 2.54, 2.55, 2.56, 2.57, 2.58, 2.59, 2.60, 2.61, 2.62, 2.63, 2.64, 2.65, 0.66, 2.67, 2.68, 2.69, 2.70, 2.71, 2.72, 2.73, 2.74, 2.75, 2.76, 2.77, 2.78, 2.79, 2.80, 2.81, 2.82, 2.83, 0.84, 2.85, 2.86, 2.87, 2.88, 2.89, 2.90, 2.91, 2.92, 2.93, 2.94, 2.95, 2.96, 2.97, 2.98, 2.99, or 3.00, δ may be non-optional such that the material does include the fractional part.
δ may be a range including any number named above while excluding at least one number mentioned above. For example, S may equal 0.1 to 3.0 with the exclusion of 1 and 2. In an alternative example, δ may include one or more ranges of 0.1 to 0.9, 1.1 to 1.9, or 2.1 to 2.9. In a yet another non-limiting example, δ may include one or more ranges of 0.01 to 0.99, 1.01 to 1.99, or 2.01 to 2.99.
In one or more embodiments, the oxygen vacancies within the first oxide contribute to beneficial properties of the material. Thus, the oxygen vacancies are formed and preserved on purpose, and processes which would eliminate presence of oxygen vacancies may be avoided or excluded during the material synthesis and/or use.
Oxygen vacancies in the first oxide may be characterized as a quantitatively smaller amount of oxygen atoms present in the material than expected in the parent material's crystal lattice. Oxygen vacancies are typically formed by removing an oxygen from a compound of oxygen, for example by annealing in a reducing atmosphere of N2, Ar, or the like. In another embodiment, annealing may be carried out in a vacuum furnace. The oxygen vacancies may render the material non-stoichiometric or deviating from stoichiometry such that the elemental composition of the material may not be represented by a ratio of well-defined natural numbers. The material; however, may be stoichiometric.
In some applications, oxygen vacancies may be perceived as undesirable defects influencing structural, electrical, optical, dissociative and reductive properties, or other properties in a manner which is not suitable for various applications. In contrast, the materials disclosed herein have desirable properties due to oxygen vacancies being present. While a base or parent compound and a material with oxygen vacancies may have common morphology, structure, or lattice to a certain degree, their properties may significantly differ. Such is the case with the disclosed material having oxygen-deficient stoichiometry. The first oxide has crystalline structure alike the parental MgTi2O5 phase. But even the crystalline structure differs due to the oxygen deficiencies. For example, the first oxide's lattice may include extra bonds or lack bonds in spaces where the paternal phase includes a bond. An example of the structural differences of the parental MgTi2O5 phase and the first oxide may be seen in
As can be seen in
Without limiting the disclosure to a single theory, it is believed that due to presence of the oxygen vacancies, the disclosed first oxide has very different properties than the parental phase, for example electrical conductivity as the oxygen vacancy functions as the dominant charge carrier for electrical conduction in the material. An additional difference may be observed in its physical appearance. While the parental MgTi2O5 phase is white in color, the disclosed first oxygen has a black to gray appearance with deep blue hue, indicative of the oxygen vacancies. An example of the synthesized first oxide can be seen in
The disclosed material has good electrical conductivity. The first oxide and the second oxide contribute to the disclosed material's overall good electrical conductivity. The Mg1−xTi2+xO5-δ and/or MgTi2O5-δ may have an electrical conductivity of about 0.01-15, 1.5-12, or 2-10 S/m at room temperature in ambient environments. The Mg1−xTi2+xO5-δ and/or MgTi2O5-δ may have an electrical conductivity of about, at least about, or up to about 0.01, 0.02, 0.03, 0.04, 0.05, 0.06, 0.07, 0.08, 0.09, 0.10, 0.12, 0.15, 0.17, 0.20, 0.22, 0.25, 0.27, 0.30, 0.32, 0.35, 0.37, 0.40, 0.42, 0.45, 0.47, 0.50, 0.55, 0.60, 0.65, 0.70, 0.75, 0.80, 0.85, 0.90, 0.95, 1.0, 1.2, 1.5, 1.7, 2.0, 2.2, 2.5, 2.7, 3.0, 3.2, 3.5, 3.7, 4.0, 4.2, 4.5, 4.7, 5.0, 5.2, 5.5, 5.7, 6.0, 6.2, 6.5, 6.7, 7.0, 7.2, 7.5, 7.7, 8.0, 8.2, 8.5, 8.7, 9.0, 9.2, 9.5, 9.7, 10, 10.2, 10.5, 10.7, 11, 11.2, 11.5, 11.7, 12, 12.2, 12.5, 12.7, 13, 13.2, 13.5, 13.7, 14, 14.2, 14.5, 14.7, or 15 S/m, or any range in between, at room temperature in ambient environments.
Electrical conductivity may be expressed via a bandgap (Eg), also called an energy gap. The band gap refers to the energy difference between the top of the valence band and the bottom of conduction band. Substances with large bandgaps are typically insulators, and those with smaller bandgaps are called semiconductors. Conductors either have no or zero bandgap (i.e., metallic) or very small bandgaps such as (<1 eV) (i.e., semi-metallic).
The first-principles DFT calculations were carried out to examine conductive behavior of Mg1−xTi2+xO5-δ and/or MgTi2O5-δ The calculations were carried out within the Vienna Ab-initio Simulation Package (VASP) with projected augmented wave potentials and Perdew-Burke-Ernzerhof (PBE) formulation of the generalized gradient approximation (GGA). A plane-wave basis set cutoff energy of 520 eV was used.
For the atomistic simulation, the supercell of orthorhombic Cmcm MgTi2O5 (space group No. 63) with 12 formula unit was used with the k-point mesh of 3×3×3. From the density of state (DOS) simulation of
In contrast, as is shown in
The DFT calculations were also utilized to assess anti-corrosive behavior of the disclosed first oxide. DFT slab models were tested with hydrogen adsorption and dissociation reactions. Hydrogen dissociation reactions were tested on (110) MgTi2O5, (110) MgTi2O5-δ, (101) TiO2 (anatase), (110) TiO2 (rutile), and (001) TiO structures of which are shown in
As Table 1 shows, (110) MgTi2O5-δ has the largest hydrogen adsorption energy, compared to other tested chemical species. This finding directly correlates to the highest H resistivity for (110) MgTi2O5-δ among the group of the tested species. In addition, (110) MgTi2O5-δ shows a minimum hydrogen coverage (i.e., least hydrogen dissociation).
The disclosed first oxide may have a nominal chemical composition of about 25-40, 28-35, or 30-33 mol % MgO and 75-60, 72-65, or 70-66 mol % TiO+TiO2 mixture. The Mg and Ti mol ratio Mg/Ti may be about 0.01-0.8, 0.1-0.60, or 0.25-0.5. The Mg and Ti mol ratio Mg/Ti may be about 0.01, 0.02, 0.03, 0.04, 0.05, 0.06, 0.07, 0.08, 0.09, 0.10, 0.11, 0.12, 0.13, 0.14, 0.15, 0.16, 0.17, 0.18, 0.19, 0.20, 0.21, 0.22, 0.23, 0.24, 0.25, 0.26, 0.27, 0.28, 0.29, 0.30, 0.31, 0.32, 0.33, 0.34, 0.35, 0.36, 0.37, 0.38, 0.39, 0.40, 0.41, 0.42, 0.43, 0.44, 0.45, 0.46, 0.47, 0.48, 0.49, 0.50, 0.51, 0.52, 0.53, 0.54, 0.55, 0.56, 0.57, 0.58, 0.59, 0.60, 0.61, 0.62, 0.63, 0.64, 0.65, 0.66, 0.67, 0.68, 0.69, 0.70, 0.71, 0.72, 0.73, 0.74, 0.75, 0.76, 0.77, 0.78, 0.79, 0.80, or a range including any two numbers named herein. Non-limiting example Mg/Ti ratio values include the following Mg0.4Ti2.6O5 with the Mg/Ti ratio of 0.15, Mg0.5Ti2.5O5 with the Mg/Ti ratio of 0.2, Mg0.6Ti2.4O5 with the Mg/Ti ratio of 0.25, Mg0.7Ti2.3O5 with the Mg/Ti ratio of 0.30, Mg0.8Ti2.2O5 with the Mg/Ti ratio of 0.36, or Mg0.9Ti2.1O5 with the Mg/Ti ratio of 0.43.
In one or more embodiments, the method of preparing the first oxide is disclosed. The synthesis may include preparing dry powders of MgO, TiO, and/or TiO2. The method may include forming a mixture of the MgO, TiO, and/or TiO2. The method may include mixing a first powder of MgO and a second powder premixture of TiO/TiO2 or TiO. The method may include drying the one or more compounds to be included in the mixture. Drying may be conducted in vacuum or ultra-high vacuum, N2, Ar, or Ar/H2 environment. Ultra-high vacuum refers to a regime of pressures lower than about 10−7 pascal or 100 nanopascals (10−9 mbar, ˜10−9 torr).
The mixture may be compressed into any shape or configuration, for example in a mold. A non-limiting example may be compressed pellets. The compressed mixture may be heated by sintering for an amount of time. Sintering is a process of compacting and forming a solid mass of a material by heat and/or pressure without melting it to the point of liquefication or the material's melting point.
The amount of time may be an amount needed for the powder particles to fuse together and create a solid piece, and/or for the compressed material to change appearance from light gray to blue-black. The sintering may be carried out at a temperature which is below the powder mixture's melting point. The temperature may range from about 400 to 2000° C., 800 to 1800° C., or 1200 to 1500° C. in vacuum, N2, Ar, or Ar/H2 environment.
The disclosed material may be formed as a foam or as a composite, for example including polymeric binders.
The disclosed material may be prepared as nanomaterial or micromaterial. The nano- or micro-material may be in the form of fibers, rods, network, cloth, felt, etc. The nanofiber may have a diameter of about 10 to 250, 30 to 200, or 50 to 100 nm and axial length of about 50 to 950, 100 to 800, or 200 to 600 nm. The microfiber may have a diameter of about 50 nm to 5 μm, 250 nm to 2 μm, or 500 nm to 1 μm and axial length of about 500 nm to 500 μm, 250 nm to 250 μm, or 100 nm to 100 μm. The nano- and/or micro-material may show presence of increased facets, including, but not limited to facet (110), (023), (002), (020), (200), (023), and/or (021). The nano-sized material, micro-sized material, or both may be porous. The nano-sized material, micro-sized material, or both may be sintered. The nano-sized material, micro-sized material, or both may be beneficial in the PTL application in a PEM electrolyzer. The PTL may be a cathode PTL, anode PTL, or both.
The amount of oxygen vacancies may be tailored depending on the needs of a specific application. The amount of oxygen vacancies may be introduced, controlled, or altered by controlling, adjusting, or controlling the sintering temperature. The amount of oxygen vacancies may be controlled by the TiO/TiO2 ratio in the powder mixture. The TiO/TiO2 ratio may be about 0:100, 1:99, 10:90, 20:80, 30:70, 40:80: 50:50, 60:40, 70:30, 80:20, 90:10, 99:1, or 100:0.
It was surprisingly discovered that in contrast to sintering, annealing destroys oxygen vacancies in the disclosed material. Since the oxygen vacancies are desirable in the disclosed material, annealing, as a process of minimizing crystal defects through a heat treatment and involving heating a material above its recrystallization temperature, maintaining a suitable temperature for a certain amount of time, and then cooling in air, should be avoided.
Set A
To verify the DFT-derived results, the first oxide was synthesized and tested according to the methods described below.
The first oxide was synthesized by the following method using a dry MgO, TiO and TiO2 powder mixture. MgO powder was dried at 120° C. for 2 hours in Ar environment. Alternatively, Mg carbonate or another type of Mg-bearing precursor may be used. The dried powder was then mixed with TiO/TiO2 powder to form a mixture. Alternatively, TiO2 or other type of Ti-bearing precursors (TiOx, Ti nitrate, chloride, etc.) may be used. The mixture was pressed into pellets measuring about 12 mm in diameter and 2 mm in thickness under 3000 psi uniaxial load. The as-pressed pellets had a light grey color. The compacted pellets were then loaded in a Al2O3 crucible and heated-up for reactive sintering (e.g. at 1450° C.) in vacuum environment (10−3 torr) for 10 hours. Alternatively, reducing gas agents such as N2, Ar, or H2, or a mixture thereof may be used. After sintering, the pellets appeared to be black in color with a blue hue. The method was used to prepare five batches of pellets, each batch containing three to four pellets.
Five sintered pellets, one from each batch, where Au sputtered on both sides of the surface. Afterwards, the pellets were assembled in an EL-Cell® ECC cell. Constant current was applied and voltage values were recorded after about 10 min until the voltage reading stabilized. This step was repeated several times at different currents. Resistance and DC electrical conductivity was calculated by linear slope from fitting the V-I data.
X-ray photoemission spectroscopy (XPS) and optical microscopy was used to assess physical characteristics of the first oxide in several pellets from two different batches. For the purposes of the observation, some of the pellets were annealed. The pellets were compared to comparative pellets of TiO2. The XPS studies of the pellets were performed using a PHI XPS system equipped with an Al X-ray source (incident photon energy of 1486.7 eV). The aperture size was set to about 1.1 mm in diameter. The binding energy of the obtained XPS spectra was calibrated with respect to the C is peak of adventitious carbon at 284.8 eV.
The sintered pellets were assessed optically. The surface of the sintered pellets can be seen in
Electrical conductivity was assessed for the as-synthesized pellets at about 1.7-8 S/m while the annealed pellets shown at
The as synthesized pellets were further tested for corrosion resistance. Corrosion current measurements were carried out in a three-electrode liquid cell setup. Counter electrode was about 16 cm2 Pt-mesh. The reference electrode was a standard Ag/AgCl electrode in KCl solution. Pellets were used as the working electrode with an effective area of about 0.5 cm2. For each measurement, one pellet was measured at a time. In total, three pellets were measured. For static corrosion current measurement, pH=2 sulfuric acid was used as electrolyte at 60° C. Static corrosion current was recorded at 1.0 V bias vs Ag/AgCl reference electrode. The corrosion voltage test may be up to 2 V vs. reference electrode, suitable for OER conditions in PEME.
The results of the corrosion current measurements are shown in
The Mg1−xTi2+xO5-δ and/or MgTi2O5-δ may have corrosion resistance (static corrosion current density) of less than about 0.5-5, 1-3, or 1.5-2.5 pA cm2 at pH of 2 at a temperature of about 0 to 80° C., 10 to 60° C., or 20 to 40° C. The Mg1−xTi2+xO5-δ and/or MgTi2Os5a may have corrosion resistance of less than about 5.0, 4.0, 3.0, 2.5, 2.0, 1.8, 1.6, 1.4, 1.2, 1.0, 0.9, 0.8, 0.7, 0.6, 0.5, 0.4, 0.3, 0.2, or 0.1 μA cm−2 at pH of 2 at a temperature of about 0 to 80° C., 10 to 60° C., or 20 to 40° C.
The pellets were also tested for chemical resistivity or inertness. Chemical inertness relates to the first oxide's reactivity with compounds present in the acidic fuel cell environment such as H3O+, F−, and SO4−. One pristine pellet was crushed into powder, which was tested in Aqua Regia (concentrated HNO3 and HCl mixture with 3:1 ratio) heated to 100-150° C. The powder did not dissolve, which indicated good chemical stability.
In one or more non-limiting embodiments, the disclosed material, including the first oxide of the formula (Ia), (Ib), or both, and/or the second oxide of formula (II), may be used as a catalyst support in an electrochemical cell, the PEMFC, or PEME. In a PEMFC, an anode and a cathode each may include a catalyst facilitating the reactions of oxygen and hydrogen. The anode catalyst oxidizes the fuel into the hydrogen protons and electrons at the anode while the cathode catalyst catalyzes oxygen reduction reaction which results in formation of water. Due to a more complicated chemistry at the cathode, a higher loading of a catalyst is usually needed at the cathode than at the anode to increase the reaction speed.
A suitable catalyst must be stable enough to withstand the corrosive environment at the cathode as well as sufficiently chemically active to be able to reduce 02. The catalyst must be also selective enough to produce the desired product while minimizing production of undesirable intermediates. The catalyst layer should be also capable of facilitating release of product water from the catalyst surface to free up catalytic sites once the reaction is complete.
A variety of noble metals have been used as a catalyst. The most commonly-used catalyst is platinum (Pt) due to its excellent catalytic activity and moderate stability to withstand its harsh operating condition. Indeed, Pt is one of the few elements capable of withstanding the acidic (PH<2) operation environment of the fuel cell.
Typically, to increase stability of the catalysts and to prevent their physical detachment from the system, the catalyst materials are typically affixed to catalyst support materials, which are typically solid materials with a high surface area. The catalyst support itself needs to be inert to prevent affecting the catalytic reactions. The most common catalyst supports for PEMFC include graphite, carbon nanofibers, carbon nanotubes, nanospheres, nanoellipsoids, nanorods, the like, or a combination thereof. Yet, oxidation of these support materials under the fuel cell operating conditions may occur, especially during the start-up/shutdown processes, which may in turn lead to degradation of the catalyst which may be limiting the PEMFC lifetime. Additionally, as was mentioned above, while the carbon-based support materials described above are acceptable and widely used in the PEMFC and PEME cathodes, PEME anodes need to operate at even higher voltage for carrying out OER reactions. Thus, the highly oxidizing PEME environment may lead to accelerated corrosion of the support materials, which in turn may lower function of the catalyst layer porous structure. For carbon-based supports, the phenomenon is known as carbon corrosion. Therefore, various metal oxides have been studied as a possible alternative catalyst support, as opposed to carbon, due to their tendency to improve the catalyst stability and resistance against further oxidation. For example, TiOx, NbOx, SnOx, and other doped metal oxides have been investigated as possible support materials for OER catalysts. But even these metal oxides lose conductivity over time.
Any catalyst support material needs to meet certain criteria—to be stable in the PEMFC and PEME operating conditions, which is usually acidic (i.e., low pH, from pH 1 to 4), and to withstand different voltages which are being applied to the electrochemical cell: typically, 0 V up to ˜1.2 V vs. SHE for PEMFC and above 1.6 V vs. SHE for PEME.
Among different metal oxides to be used as catalyst support materials in a PEMFC electrode, TiO2 and SnO2 have been disclosed as leading candidates. This is due to their stability in the aqueous electrochemical system for TiO2 and SnO2: forming a stable oxide where pH can vary from 1 to 4 (i.e., acidic) and voltages between 0 to 1.23 V can also affect the local environment during the PEMFC operation. Recently, Sn-doped TiO2 was also tested as a catalyst support material for Pt catalyst and reported the following: 1) doping up to 10% Sn in TiO2 resulted in an increase in the mass activity; 2) catalyst support with 23 to 40% Sn doping in TiO2 required much less platinum, and, 3) Sn-doped TiO2 was stable in the acidic conditions at 80° C. at <28% doping of Sn in TiO2.
In one or more embodiments, the material disclosed herein including the first oxide of the formula (Ia), (Ib), or both, and/or the second oxide of formula (II) may be used as a support for a PEMFC catalyst in the fuel cell application, on a cathode, anode, or both, or as a cathode and/or anode catalyst support in PEME. The catalyst may be a noble metal or noble-metal free catalyst. A non-limiting example of a catalyst may be Pt, Pd, Au, Ir, Rh, Ru, or a combination thereof. The catalyst may be an oxidation reduction reaction (ORR) catalyst.
The disclosed material may have porosity similar to high area surface carbon (with BET surface area of about 1 to 700 m2/g). The disclosed material may be less porous than carbon. The disclosed support material may have an average particle size less than about 200 nm. The particle size may be about 20 to 200 nm, 25 to 150 nm, or 30 to 100 nm. Alternatively, the particle size may be about 200 to 600 nm, 300 to 550 nm, or 400 to 500 nm. The particle size of the catalyst support including the disclosed material may be about 20, 30, 40, 50, 60, 70, 80, 90, 100, 110, 120, 130, 140, 150, 160, 170, 180, 190, 200, 210, 220, 230, 240, 250, 260, 270, 280, 290, 300, 310, 320, 330, 340, 350, 360, 370, 380, 390, 400, 410, 420, 430, 440, 450, 460, 470, 480, 490, 500, 510, 520, 530, 540, 550, 560, 570, 580, 590, 600 nm, or a range including any two numbers disclosed above.
The catalyst may be deposited onto the support including the disclosed material either forming one or more island(s) of catalyst on the catalyst support, as is shown in
The catalyst support material including Mg1−xTi2+xO5-δ and/or MgTi2O5-δ is chemically stable in acidic environment and has high electrochemical stability against corrosion and oxidation environments during fuel cell operation conditions, as is demonstrated herein.
DFT calculations were performed to construct the interface between a Pt metal catalyst and Mg1−xTi2+xO5-δ and/or MgTi2O5-δ. DFT calculations were carried out within the Vienna Ab-initio Simulation Package (VASP) with projected augmented wave potentials and Perdew-Burke-Ernzerhof (PBE) formulation of the generalized gradient approximation (GGA). A plane-wave basis set cutoff energy of 520 eV was used. The DFT calculations were used to verify that Pt and Mg1−xTi2+xO5-δ and/or MgTi2O5-δ may form a stable interface, which may enable utilization of Mg1−xTi2+xO5-δ and/or MgTi2O5-δ as an oxide support material for a PEMFC or PEME catalyst.
Table 2 below shows the DFT-calculated interfacial energy between a Pt catalyst and Mg1−xTi2+xO5-δ and/or MgTi2O5-δ support. Specifically, energetically-stable Pt surface facets (111), (100), and (110) were examined on the (110) MgTi2O5-δ Table 2 illustrates that the calculated DFT interfacial energies between (110) MgTi2O5-δ and Pt catalyst (regardless of the facets) are predicted to be a negative value. A negative DFT interfacial energy indicates that two chemical systems will form a stable interface. Table 2 further shows DFT interfacial energies of Pt on TiO2 and SnO2 for comparison. As can be seen in Table 2, the interfacial energy for MgTi2O5-δ and SnO2/TiO2 are comparable. For the DFT calculations, ΔEmt=E0.total−(E0,Pt,surf+E0.MOx), where the internal energy (E0) may be obtained from the DFT calculations.
Table 1 further shows that (100) Pt may bind most strongly on (110) MgTi2O5-δ, while (110) Pt may bind less strongly on (110) MgTi2O5-δ. While the (111) facet seems to be the most energetically favored surface facet in Pt nanoparticles, (110) and (100) are also observed at the corner and edge of the Pt particles. Depending on the synthesis temperature, time, pH, precursor materials, and route, it is possible to control the size and shape of Pt nanoparticles, as shown in
Conductive and anti-corrosive behavior of the disclosed material as a catalyst support was further investigated. Table 3 below shows DFT binding energies (ΔEb) of H2O and H3O on Pt supported by various metal oxide supports. Relative binding energies (ΔErel,b) are also provided, where the binding energies on pure Pt (111) are used as the reference (i.e., zero energy). The calculated binding energies of H2O and H3O of Pt supported on MgTi2O5-δ are between Pt supported on SnO2 and TiO2. This indicates that Pt on MgTi2O5-δ may provide more stability than Pt supported on SnO2 while it can provide more reactivity compared to Pt supported on TiO2.
As can be seen in Table 3, the relative binding energies of H2O for Pt on MgTi2O5-δ range between −0.063 and −0.157 eV. For the case of H3O, the binding energies vary from −0.090 eV to −0.027 eV. For both of these cases, the binding energies are lower than Pt supported on TiO2, while higher than Pt supported on SnO2. Thus, as was stated above, Pt on MgTi2O5-δ may have more “stability” against the reactant than Pt supported on SnO2 and may have more “reactivity” than Pt on TiO2. Additionally, the MgTi2O5-δ's anti-corrosive behavior and enhanced electronic conductivity discussed above and referenced in
The disclosed catalyst support material may be prepared by a variety of methods including, but not limited to a solution-based process, a solid-state process, a heat-treatment, and/or electrochemical methods. The catalyst support material may be un-doped, and/or doped partially with nitrogen, carbon, fluorine, the like, or other elements to further enhance electronic conductivities. Non-limiting examples of other elements may include other d° metals such as Zr4+, Hf1+, V5+, and/or Cr6+, and/or d10 metals such as Zn2+, Ga3+, and/or Pb4+, as well as Al3+ (no d electrons), where d0 and d10 metals and Al3+ are typically more difficult to be oxidized.
A non-limiting example preparation method may include dissolving metal-containing precursor chemicals such as M(NO3)x, MClx, M(OH)x, and MOx, where M=Mg and Ti in a solvent to form an initial mixture. The solvent may be water or an organic solvent. The pH of the solution may be adjusted, maintained, or controlled by the presence of oxidizing or reducing chemicals. The initial mixture may be heat-treated between about 100 to 2000° C., 200 to 1500° C., or 300 to 1000° C. with a various aging time of about 1, 2, 3, 4, 8, 12, 16, 24, 36, 48, 60, or 72 hours to form the catalyst support material. During the heat treatment, the gas environment may be controlled by N2, Ar, H2, O2, air, and/or vacuum. A catalyst material such as Pt may be deposited on the catalyst support material afterwards, either using solid-state, solution-based method, and/or various deposition techniques.
Various size of oxide precursor materials such as MgO, TiO, TiO2, Mg(OH)2, or the like may be mixed and synthesized via a solid-state method such as a ball-milling process, co-precipitation process (e.g., solution-based process), sol-gel process, hydrothermal process, or the like, followed by a secondary heat treatment.
The herein-disclosed catalyst supports may be prepared into high surface area particles by a hydrothermal method followed by a subsequent annealing process in an oxygen-free atmosphere. The non-limiting example BET of the herein-disclosed catalyst support may be about 100 to 1500, 150 to 850, or 200 to 550 m2/g. The non-limiting example BET of the herein-disclosed catalyst support may be about, at least about, or up to about 100, 150, 200, 250, 300, 350, 400, 450, 500, 550, 600, 650, 700, 750, 800, 850, 900, 950, 1000, 1050, 1100, 1150, 1200, 1250, 1300, 1350, 1400, 1450, or 1500 m2/g or any range in between. In comparison, Vulcan XC-72 material typically has BET specific area of 250 m2/g: high surface area carbons may have the BET specific area of up to about 1,500 m2/g: e.g., Ketjen Black EC 600 JD, Ultra High Surface Area Carbon (USAC), and so on.
Another non-limiting example BET area of the herein-disclosed catalyst support may be below 100 m2/g such as 0.1 to 99, 1 to 50, or 5 to 25 m2/g. The BET area of the herein-disclosed catalyst support may be about, at least about, or up to about 0.1, 0.2, 0.3, 0.4, 0.5, 0.6, 0.7, 0.8, 0.9, 1.0, 1.2, 1.4, 1.6, 1.8, 2.0, 2.2, 2.4, 2.6, 2.8, 3.0, 3.2, 3.4, 3.6, 3.8, 4.0, 4.2, 4.4, 4.6, 4.8, 5.0, 5.5, 6.0, 6.5, 7.0, 7.5, 8.0, 8.5, 9.0, 9.5, 10, 11, 12, 13, 14, 15, 16, 17, 18, 19, 20, 22, 24, 26, 28, 30, 32, 34, 36, 38, 40, 42, 44, 46, 48, 50, 55, 60, 65, 70, 75, 80, 85, 90, 95, or 99 m2/g or any range in between.
Alternatively, the herein-disclosed catalyst support material may be prepared by a chemical reaction under a relatively high temperature of about 400 to 2000° C., 800 to 1800° C., or 1200 to 1500° C. in vacuum, N2, Ar, or Ar/H2 environment followed by mechanical milling. The preparation atmosphere should be kept free of oxygen such that oxygen is not supplied during the reaction and is actively removed from the reaction environment. The herein-disclosed catalyst supports may be prepared by a colloidal synthesis route followed by subsequent annealing steps in varying atmosphere. The herein-disclosed catalyst support may be prepared by a combustion synthesis or flame synthesize method followed by subsequent annealing steps in an oxygen-free environment.
The disclosed material including the first oxide and the second oxide may be used for catalysis in a variety of applications including PEMFC, anion exchange membrane fuel cell (AEMFC), either at the cathode or the anode, proton exchange membrane electrolyzer (PEME), chemical synthesis, air purification including purifying exhaust from an internal combustion engine, photo-catalysis for water splitting cells, or photo-catalysis of redox media for water cleaning.
The herein-disclosed catalyst support material may be further mixed with carbon and/or another type of conductive polymer to increase conductivity. Carbon includes, but is not limited to, amorphous carbon, Denka black, Ketjen black, acetylene black, carbon nanotube, carbon fibers, graphene, graphite, graphyne, graphene oxide, reduced graphene oxide, etc. The ratio of the mixture may be about 1:1, 1:2, 1:3, 1:4, 1:5, 1:6, 1:7, 1:8, 1:9, 1:10, 10:1, 9:1, 8:1, 7:1, 6:1, 5:1, 4:1, 3:1, or 2:1. Alternatively, carbon and/or another type of additional support material may form one or more additional sublayers, serving as a support for the disclosed material.
The herein-disclosed catalyst support material may be mixed with one or more types of catalyst support materials such as additional oxides, carbides, or intermetallic compounds. Example oxide materials may include SnO2, MoO3, Nb2O5, Ta2O5, TiO2, WO3, SnMo4O6, and/or TiNb3O6, GeO2, MoO2, NbO2, SnO, Ti3O5, SnWO4, WO2, Nb2SnO6, Sn2WO5, SnGeO3, Ta2SnO6, TiSn2O4, Ti6O, or mixtures thereof. Example carbides may include Nb6C5, Mo2C, Ta2C, Ti8C5, WC, TaC, Nb2SnC, Ti2GeC, Ti3SnC2, Ti3GeC2, MoC, or mixtures thereof. Non-limiting examples of binary or ternary intermetallic compounds may be MoW, NbSn2, Nb3Sn, Sn2Mo, TaSn2, Ta3Sn, TaW3, TiMo, TiMo3, Ti2Mo, Ti3Mo, TiNb, Ti2Sn, Ti2Sn3, Ti3Sn. Ti6Sn5, NbMo2W, TaMo2W, TiMo2W, Ti2NbSn, GeMo3, Ge2Mo, NbGe2, Nb5Ge3, SnGe, TaGe2, Ta3Ge, Ta5Ge3, TiGe2, Ti5Ge3, Ti6Ge5, or mixtures thereof. Depending on the secondary heat-treatment conditions such as temperature, presence of oxidizing/reducing agents, the amount of oxides (as well as their compositions) in the surface film and bulk region of the intermetallic component may be further controlled.
Set B
To validate the DFT-calculated results, MgTi2O5-δ was used to form pellets by a method described under EXAMPLES, Set A above. Subsequently, a catalyst material including Pt was sputtered onto the pellets, and the catalyst support with the catalyst were exposed to annealing at 600° C. for 10 hours.
The anticorrosive, conductive material disclosed herein may include the first oxide of the formula (Ia), (Ib), or both described above in a combination with a second oxide having a general formula (II):
TiaOb (II),
where,
1<=a<=20 and 1<=b<=30, wherein a and b may be any number between 1 and 20 or 30, respectively, optionally including a fractional part such as decimals, a and/or b may be 1, 2, 3, 4, 5, 6, 7, 8, 9, 10, 11, 12, 13, 14, 15, 16, 17, 18, 19, 20, 21, 22, 23, 24, 25, 26, 27, 28, 29, or 30 or any ranges of numbers within the span of 1 to 20 or 1 to 30, respectively.
Non-limiting example compounds of the second oxide having the formula (II) include TiO, TiO2, Ti2O3, Ti3O5, Ti2O, Ti3O, Ti6O, Ti4O7, Ti6O11, Ti5O9, Ti5O13, Ti19O30, Ti7O13, Ti5O8, and Ti13O22. The second oxide may be Ti2O3. The second oxide may be an oxide described above. The second oxide may be any and all oxides described above with the exception of at least one of the oxides described above. The second oxide may include a variety of facets such as (012), (110), (010), (001), etc.
Depending on the composition and crystal structure of TiaOb, the second oxide of formula (II) may be metallic (Eg=0), semi-metallic (0<Eg<=1 eV), semiconductor (1<=Eg<=2 eV), or insulating (Eg>2 eV).
The second oxide of formula (II) may form a part of the disclosed material or matrix including the first oxide of the formula (Ia), (Ib), or both. The second oxide may exist as a part of a polycrystalline structure, be a part of or exist within the MgTi2O5 matrix. The second oxide may exist as a segregated polycrystalline phase and/or be located at, on, or near grain boundaries, i.e. within 1 nm to 100 μm (100,000 nm), 10 nm to 10 μm (10,000 nm), or 100 nm to 1 μm (1,000 nm) from the grain boundaries. The second oxide may exist as a segregated polycrystalline phase within the distance of about 1, 5, 10, 50, 100, 500, 1000, 5000, 10,000, 50,000, or 100,000 nm from the grain boundaries. Depending on the materials system, grain sizes can range from about 1 to 100, 5 to 80, or 10 to 60 μm.
The grain size may range from 1, 2, 3, 4, 5, 6, 7, 8, 9, 10, 12, 14, 16, 18, 20, 22, 24, 26, 28, 30, 32, 34, 36, 38, 40, 42, 44, 46, 48, 50, 52, 54, 56, 58, 60, 62, 64, 66, 68, 70, 72, 74, 76, 78, 80, 82, 84, 86, 88, 90, 92, 94, 96, 98, or 100 μm. Alternatively, the size of dislocations may begin to approach the size of the grains. At a grain size of about 5 to 15, 7 to 12, or 8 to 10 nm, one or two dislocations may fit inside a grain. The grain size may be about 5, 6, 7, 8, 9, 10, 11, 12, 13, 14, or 15 nm. Additionally, the second oxide of the formula (II) may form a grain, where the size may vary from about 10 to 50, 15 to 40, or 20 to 30 μm, next to the grain boundary of the first oxide of the formula (Ia), (Ib), or both. The grain size may be about 10, 12, 14, 16, 18, 20, 22, 24, 26, 28, 30, 32, 34, 36, 38, 40, 42, 44, 46, 48, or 50 μm.
The amount of the second oxide within the disclosed material, matrix, or total composite may be about, at least about, or up to about 0.5 to 50, 2 to 30, or 3 to 15 wt. %, based on the total amount of material, matrix, or composite. The amount may be about, at least about, or up to about 0.5, 1, 1.5, 2, 2.5, 3, 3.5, 4, 4.5, 5, 5.5, 6, 6.5, 7, 7.5, 8, 8.5, 9, 9.5, 10, 10.5, 11, 11.5, 12, 12.5, 13, 13.5, 14, 14.5, 15, 15.5, 16, 16.5, 17, 17.5, 18, 18.5, 19, 19.5, 20, 20.5, 21, 21.5, 22, 22.5, 23, 23.5, 24, 24.5, 25, 25.5, 26, 26.5, 27, 27.5, 28, 28.5, 29, 29.5, 30, 30.5, 31, 31.5, 32, 32.5, 33, 33.5, 34, 34.5, 35, 35.5, 36, 36.5, 37, 37.5, 38, 38.5, 39, 39.5, 40, 40.5, 41, 41.5, 42, 42.5, 43, 43.5, 44, 44.5, 45, 45.5, 46, 46.5, 47, 47.5, 48, 48.5, 49, 49.5, or 50 wt. %, based on the total amount of material, matrix, or composite.
The amount of the second oxide, which is detectable using X-ray diffraction technique, may be above about 5 wt. %, based on the total amount of material, matrix, or composite. In another embodiment, the amount of the second oxide, detectable with advanced techniques including synchrotron-based analysis, induction coupled plasma mass spectroscopy, x-ray photon spectroscopy, or high-resolution transmission electron microscope, may be less than about 0.5, 1.5, or 2.5 wt. %.
The oxide of formula (II) may be conductive and anti-corrosive at the same time, contributing to desirable properties of the matrix, material, or composition including the first oxide of the formula (Ia)(Ib), or both. DFT calculations were conducted to confirm conductive and anti-corrosive behavior of the second oxide.
For example,
The DFT calculations described above revealed that the (012) facet is the most dominant surface facet for R-3c Ti2O3 with the calculated surface energy of 1.01 J/m2. The DFT calculations were also used to assess anti-corrosive behavior of the (012) Ti2O3 facet. Table 3 below shows a comparison of a single atom hydrogen adsorption energy on TiOx and MgTi2O5-δ.
A negative DFT-calculated adsorption energy indicates that adsorbate (e.g., a single hydrogen atom) binds more strongly to the substrate. Thus, to protect the substrate from hydrogen (i.e., acidic environment), it is most desirable to have a high adsorption energy. As Table 4 above demonstrates, Ti2O3 has the highest adsorption energy among other Ti—O bearing compounds. As was described above, and is confirmed in Table 4, the single hydrogen DFT-calculated adsorption energy for MgTi2O5-δ is the most positive among the calculated materials.
Regarding dissociation energy, for anti-corrosive and conductive behavior, it is most desirable to have high hydrogen dissociation energy and low hydrogen coverage.
The first-principles DFT calculations were carried out to examine conductive behavior of Ti2O3. The calculations were carried out within the Vienna Ab-initio Simulation Package (VASP) with projected augmented wave potentials and Perdew-Burke-Ernzerhof (PBE) formulation of the generalized gradient approximation (GGA). A plane-wave basis set cutoff energy of 520 eV was used.
From the DOS simulation of
The material properties of TiaOb may be tuned similarly as with the oxide of the formula (Ia), (Ib), for example by introducing oxygen vacancies, by cation doping, or anion doping. Alteration of material properties may be provided by a variety of methods, for example by using different chemical precursors or by controlling the heat treatment environment (e.g., use of oxidizing/reducing gas).
A non-limiting example of a cation dopant may include but is not limited to Ge, Nb, Mo, Sn, Ta, W, or their combination. The oxide of formula (II) may be mixed with one or more conducting agents such as carbon and/or one or more conductive polymers.
A method of producing the disclosed material including the first and second oxides is disclosed herein. The method may include producing the first oxide as was described above with respect to the preparation of the first oxide of formula (Ia), (Ib), or both.
The method may include preparing the second oxide of formula (II). The second oxide may be prepared as nanoparticles. A preparation method may include, for example, a water hydrolysis and precipitation methods followed by annealing in vacuum or in a reducing environment such as N2, Ar, H2, H2/N2, H2/Ar, etc.
Alternatively, the second oxide nanoparticles may be prepared by a hydro-thermal reaction followed by an annealing process in vacuum or reducing environments such as N2, Ar, H2, H2/N2, H2/Ar, etc.
The method may include preparing the second oxide as a thin film coating from a few nm to 250 μm thick, which may be produced by physical vapor deposition followed by an annealing step in vacuum or reducing environments such as N2, Ar, H2, H2/N2, H2/Ar, etc. The film thickness may be about, up to about, or at least about 5 nm to 250 μm (250,000 nm), 50 nm to 25 μm (25,000 nm), or 500 to 2.5 μm (2,500 nm). The film thickness may be about, up to about, or at least about 5, 10, 25, 50, 100, 250, 500, 1000, 1200, 5000, 10,000, 25,000, 50,000, 100,000, or 250,000 nm.
The method may include combining the first and second metal oxides, for example embedding the second oxide within a matrix of the first oxide. The method may include controlling the oxidizing/reducing environment to control the oxidation state of Ti. For example, to synthesize more Ti2+ (similar to TiO), the method may include increasing the reducing conditions. The increasing may include controlling several factors including but not limited to gas flow, elevated temperature synthesis, choice of precursors, the like, or a combination thereof. To induce more Ti4+ character, the method may include increasing the oxidizing conditions. The oxidation state of Ti3+, similar to Ti2O3, may be also induced by controlling the annealing conditions, sintering conditions, gas environment, and choosing a different Ti-bearing precursors.
In addition, the method may include using at least two different Ti precursors which may help induce different oxidation states within a single batch. For example, mixing various ratios of TiO and TiO2 as a starting precursor may generate different oxidation states. Precursor materials may include, but are not limited to, metal chloride, metal nitrate, metal sulfate, metal carbonate, etc. Alternatively, the method may implement using a dopant (p or n type) to change the local environment. For instance, if the average oxidation state of Ti2O3-embedded Mg1−xTi2+xO5-δ and/or MgTi2O5-δ is found to be 3.7+, the method may include adding a metal dopant with common oxidation state of 4+ or higher (e.g., Sn4+, Mn4+, Ge4+, Si4+, Ru5+, V5+, Nb5+, etc.), to reduce neighboring Ti next to the dopant to lower oxidation states. Alternatively still, the method may include adding another dopant with a lower oxidation state (e.g., 2+, 3+, etc.) to increase the Ti oxidation state toward 4+.
The disclosed material may be used in applications requiring both corrosion resistance and good electrical conductivity. For example, the disclosed material may be used as a BPP coating, in a BPP bulk portion, in a BPP surface portion, or a combination thereof. Alternatively, the disclosed material may be used as an anticorrosive coating in automotive parts, aerospace parts, oil and gas plants, or large-scale manufacturing. In an alternative embodiment, the disclosed material may be used as a catalyst support material, for example for PEMFC and PEME applications or other catalytic application, as was discussed above. The disclosed material may be also utilized as a porous transport layer (PTL) in a PEME, on the cathode side, anode side, or both.
The disclosed material coating on a metal BPP may be realized by different deposition techniques. A non-limiting example may involve spray coating the disclosed material containing solvents on the BPP, followed by a drying process. The oxide may be deposited on to designated support material (carbon, metal, ceramic, etc.) during the synthesis process or as a post-treatment step. Alternatively, the method may involve physical or chemical vapor deposition. As yet another alternative, an atomic layer deposition (ALD) or a solution-based approach on to the metal substrate may take place. Depending on the choice of precursor, oxidizing or reducing environment, humidity, and substrate, the degree of oxygen vacancy in Mg1−xTi2+xO5-δ and/or MgTi2O5-δ may vary, leading to different conductivity and anti-corrosion behavior. The heat treatment temperature may range from about 150 to about 1,500° C. to yield a desired ternary oxides or doped composition. The heat treatment time may vary from about 30 seconds to about 48 hrs.
The processes, methods, or algorithms disclosed herein can be deliverable to/implemented by a processing device, controller, or computer, which can include any existing programmable electronic control unit or dedicated electronic control unit. Similarly, the processes, methods, or algorithms can be stored as data and instructions executable by a controller or computer in many forms including, but not limited to, information permanently stored on non-writable storage media such as ROM devices and information alterably stored on writeable storage media such as floppy disks, magnetic tapes, CDs, RAM devices, and other magnetic and optical media. The processes, methods, or algorithms can also be implemented in a software executable object. Alternatively, the processes, methods, or algorithms can be embodied in whole or in part using suitable hardware components, such as Application Specific Integrated Circuits (ASICs), Field-Programmable Gate Arrays (FPGAs), state machines, controllers or other hardware components or devices, or a combination of hardware, software and firmware components.
While exemplary embodiments are described above, it is not intended that these embodiments describe all possible forms encompassed by the claims. The words used in the specification are words of description rather than limitation, and it is understood that various changes can be made without departing from the spirit and scope of the disclosure. As previously described, the features of various embodiments can be combined to form further embodiments that may not be explicitly described or illustrated. While various embodiments could have been described as providing advantages or being preferred over other embodiments or prior art implementations with respect to one or more desired characteristics, those of ordinary skill in the art recognize that one or more features or characteristics can be compromised to achieve desired overall system attributes, which depend on the specific application and implementation. These attributes can include, but are not limited to cost, strength, durability, life cycle cost, marketability, appearance, packaging, size, serviceability, weight, manufacturability, ease of assembly, etc. As such, to the extent any embodiments are described as less desirable than other embodiments or prior art implementations with respect to one or more characteristics, these embodiments are not outside the scope of the disclosure and can be desirable for particular applications.
This application is a continuation-in-part of U.S. application Ser. No. 16/825,638 filed Mar. 20, 2020, now pending, which is a continuation-in-part of U.S. application Ser. No. 16/675,538 filed Nov. 6, 2019, now pending, the disclosures of which are hereby incorporated in their entirety by reference herein.
| Number | Date | Country | |
|---|---|---|---|
| Parent | 16825638 | Mar 2020 | US |
| Child | 17679480 | US | |
| Parent | 16675538 | Nov 2019 | US |
| Child | 16825638 | US |
