WO2023201708A1 - 一种复合纳米金属氧化物及其制备方法与用途 - Google Patents

一种复合纳米金属氧化物及其制备方法与用途 Download PDF

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WO2023201708A1
WO2023201708A1 PCT/CN2022/088498 CN2022088498W WO2023201708A1 WO 2023201708 A1 WO2023201708 A1 WO 2023201708A1 CN 2022088498 W CN2022088498 W CN 2022088498W WO 2023201708 A1 WO2023201708 A1 WO 2023201708A1
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elements
intermediate product
composite
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nano
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赵远云
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赵远云
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    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
    • C01G23/00—Compounds of titanium
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
    • C01G23/00—Compounds of titanium
    • C01G23/04—Oxides; Hydroxides
    • C01G23/047—Titanium dioxide

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  • the invention relates to the technical field of nanomaterials, and in particular to a method for preparing composite nanometal oxides and composite oxide ceramics.
  • the commonly used preparation method for nanometer metal oxides is to add alkali precipitation to a soluble metal salt solution, and then filter, dry, and calcine to obtain nanopowder.
  • the precipitated products generated by this method are colloidal hydroxides, the filtration time is long, which increases the production cycle accordingly; moreover, hydrogen bonds are easily formed between the precipitates, which can easily lead to powder during filtration, drying, and high-temperature calcination.
  • the bulk particles agglomerate and grow up, and it is difficult to obtain powder with uniform particles, good dispersion, and no hard agglomeration.
  • Composite nanometal oxides prepared by traditional methods are generally prepared by mixing powders.
  • the preparation steps of different components need to be carried out separately at least, and the process is cumbersome.
  • the various components are usually combined together through physical adsorption or simple mixing. This kind of mixing is often difficult to achieve a sufficiently uniform effect.
  • the components need to be mixed as uniformly as possible, and even in-situ compounding is required to achieve special interactions between the components to obtain special and excellent properties. Therefore, it is urgent to develop a new method to achieve in-situ composite nanometal oxides between different oxide components through a preparation process.
  • the present invention includes a total of twelve aspects from the first to the twelfth aspect:
  • a method for preparing composite nanometal oxides is characterized by including the following steps:
  • Step 1 Provide an initial alloy.
  • the composition of the initial alloy includes T-type elements and A-type elements, wherein the T-type elements include at least one of Al and Zn; the A-type elements include elements Ti, M-type sub-elements, D Class sub-elements At least two of the three types of sub-elements; among them, M-class sub-elements include Cr, V, Nb, Ta, W, Mo, Mn, Y, La, Ce, Pr, Nd, Pm, Sm, Eu , at least one of Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu; the D sub-elements include at least one of Zr and Hf; the composition of the initial alloy is mainly A x T y , Where x and y are the atomic percentage contents of corresponding various elements, and 5 ⁇ x ⁇ 55%, 45% ⁇ y ⁇ 95%; the solidification structure of the initial alloy is mainly composed of AT intermetallic compounds;
  • Step 2 A hydrogen evolution and deT reaction occurs between the initial alloy and an alkali solution.
  • the reaction interface is formed from the surface of the initial alloy at an average rate of no less than 2 ⁇ m/min during the reaction. push inwards;
  • the initial alloy and the alkali solution undergo nano-fragmentation through the hydrogen evolution and deT reaction, and are reconstructed through shape and composition to form a shape with at least one dimension in the three-dimensional direction not exceeding 500nm.
  • the initial alloy contains D-type sub-elements
  • the initial alloy and the alkali solution undergo nano-fragmentation through a hydrogen evolution and deT reaction, and are reconstructed in shape and composition to generate a shape with at least one dimension in the three-dimensional direction not exceeding 500 nm.
  • Solid substances containing M or (and) Ti; at the same time, D-type sub-elements are mainly soluble in the alkali solution at alkali concentration and temperature corresponding to a high reaction rate, or at alkali concentration and temperature corresponding to a relatively low reaction rate. Under temperature conditions, solid substances containing D are mainly generated through shape and composition reconstruction;
  • the initial alloy does not contain D sub-elements
  • collect the solid materials containing M and Ti in the reaction system to obtain a composite nanometal oxide intermediate product containing M and Ti, the shape of which has at least one shape in the three-dimensional direction.
  • the dimension scale does not exceed 500nm; and the method of compounding the M-containing intermediate product and the Ti-containing intermediate product includes in-situ embedded composite; wherein, the M-containing intermediate product and the Ti-containing intermediate product can be corresponding atoms or atomic clusters, or It can be a corresponding phase, and at least one of the M-containing intermediate product and the Ti-containing intermediate product is a phase;
  • the composite nanometal oxide intermediate product composed of the intermediate product has a shape with at least one dimension in the three-dimensional direction not exceeding 500 nm; and the D-containing intermediate product, the M-containing intermediate product, and the Ti-containing intermediate product are combined with each other in a manner including the original Site-embedded composite; wherein, D-containing intermediate products, M-containing intermediate products, and Ti-containing intermediate products can be corresponding atoms or clusters of atoms, or they can be corresponding phases, and D-containing intermediate products, M-containing intermediate products, and Ti-containing intermediate products At least one of the three intermediate products is a phase;
  • the initial alloy contains D-type sub-elements, and the D-type sub-elements are mainly dissolved in the alkali solution
  • the precipitated concentration is below C 2
  • the precipitated solid flocculent hydrogenated D is mixed with the previously formed solid matter containing M or (with) Ti, and all solid matter is collected to obtain nano-hydrogenated D and M-containing or (with) Ti.
  • the composite nanometer metal oxide intermediate product composed of Ti intermediate product has a shape with at least one dimension in the three-dimensional direction not exceeding 500nm; wherein, C 2 ⁇ C 1 , and when the composite nanometer metal oxide intermediate product also includes
  • the method of compounding the M-containing intermediate product and the Ti-containing intermediate product includes in-situ embedded composite; wherein, the M-containing intermediate product and the Ti-containing intermediate product can be corresponding atoms or atomic clusters, It can also be a corresponding phase, and at least one of the M-containing intermediate product and the Ti-containing intermediate product is a phase;
  • Step 4 Heat-treat the composite nano-metal oxide intermediate product described in Step 3 to obtain a composite nano-metal oxide with an increased degree of crystallization; which contains three types of sub-elements: Ti, M-type sub-elements, and D-type sub-elements. At least two types of sub-elements; and at least two types of sub-elements among the three types of sub-elements, namely Ti elements, M-type sub-elements and D-type sub-elements, perform composites of corresponding oxides of heterogeneous elements at the atomic/atom cluster scale or fine phase scale. .
  • step one In step one,
  • the M includes at least one of Cr, V, Nb, Ta, W, Mo, Mn, Y, and Gd;
  • T includes Al; further, T includes Zn;
  • composition of Class A elements in the initial alloy includes any one of the following four combinations:
  • the molar percentage content of the sub-type elements with dominant content in the A-type elements is less than 99%.
  • the molar proportion of Nb in the total content of Nb and Ti needs to be less than 99%;
  • the molar percentage content of the dominant sub-category elements in the A-category elements is less than 95%
  • the molar percentage content of the dominant sub-category elements in the A-category elements is less than 90%
  • the molar percentage content of the dominant sub-category elements in the A-category elements is less than 80%;
  • the molar percentage of type D sub-elements in type A elements is higher than 30%; further, the molar percentage of type D sub-elements in type A elements is higher than 60%; further, the molar percentage of type D sub-elements in type A elements is higher than 60%.
  • the mole percentage of the element is higher than 90%;
  • the molar percentage of M-type sub-elements in type A elements is higher than 30%; further, the molar percentage of M-type sub-elements in type A elements is higher than 60%; further, the molar percentage of M-type sub-elements in type A elements is higher than 30%.
  • the mole percentage of the element is higher than 90%;
  • the molar percentage of Ti in the A-type elements is higher than 30%; further, the molar percentage of Ti in the A-type elements is higher than 60%; further, the molar percentage of Ti in the A-type elements is higher than 90% ;
  • the solidification structure of the initial alloy is mainly composed of A-T intermetallic compounds; wherein, the A-T intermetallic compounds are single-phase intermetallic compounds or multi-phase intermetallic compounds; and when the A-T intermetallic compounds are multi-phase intermetallic compounds, When, it includes Ti-T intermetallic compounds, M-T intermetallic compounds, D-T intermetallic compounds, (M-D)-T intermetallic compounds, (Ti-D)-T intermetallic compounds, (Ti-M)-T intermetallic compounds Compounds, at least two of (Ti-M-D)-T intermetallic compounds;
  • A-T intermetallic compound is a single-phase intermetallic compound, it is (M-D)-T intermetallic compound, (Ti-D)-T intermetallic compound, (Ti-M)-T intermetallic compound, (Ti- One of the M-D)-T intermetallic compounds;
  • the specific phase composition of the A-T intermetallic compound is not limited, as long as it is ensured that the A-type elements are present in the A-T intermetallic compound, that is, the A-type element atoms are dispersed and distributed in the initial alloy, and are consistent with T-type element atoms are arranged adjacently; or just ensure that the initial alloy does not contain the A phase composed of A-type elements (the A-type element atoms in the A phase are aggregated and arranged in the initial alloy);
  • the initial alloy is prepared by solidifying an alloy melt containing T-type elements and A-type elements. During the alloy solidification process, a solidification structure mainly composed of A-T intermetallic compounds is formed;
  • the initial alloy does not contain T phase;
  • the T phase is a phase mainly composed of T elements;
  • the solidification rate of the initial alloy melt is 0.01K/s ⁇ 10 8 K/s;
  • the solidification rate of the initial alloy melt is 1 K/s to 10 8 K/s;
  • the shape of the initial alloy includes at least one of granular, filamentous, strip, ribbon, and flake;
  • the shape of the initial alloy has an average size in any three-dimensional direction greater than 4 ⁇ m;
  • the shape of the initial alloy has an average size in any three-dimensional direction greater than 10 ⁇ m;
  • the shape of the initial alloy has an average size in any three-dimensional direction greater than 15 ⁇ m;
  • the initial alloy when it is in strip form, it can be prepared by a method including a melt strip spinning method;
  • a larger initial alloy ingot can be prepared by a casting method and then broken into initial alloy particles.
  • the alkali solution includes at least one of NaOH, KOH, LiOH, RbOH, CsOH, Ba(OH) 2 , Ca(OH) 2 and Sr(OH) 2 solutions;
  • the solvent in the alkaline solution contains water; preferably, the solvent in the alkaline solution is water;
  • the range of C 1 is 4-30 mol/L; preferably, the range of C 1 is 5-15 mol/L; preferably, the range of C 1 is 7-15 mol/L;
  • the alkali in the alkali solution reacting with the initial alloy is an excessive dose, and the volume of the alkali solution is more than 5 times the volume of the initial alloy, so that the reaction can always be carried out at a higher alkali concentration;
  • volume of the alkali solution is more than 10 times the initial alloy volume
  • volume of the alkali solution is more than 20 times the initial alloy volume
  • the temperature of the alkali solution should only be able to ensure that the reaction interface advances inward from the initial alloy surface at an average rate of no less than 2 ⁇ m/min during the hydrogen evolution deT reaction, and the reaction process
  • the initial alloy can be nano-disintegrated through the hydrogen evolution and deT reaction, that is, the need is determined by the hydrogen evolution and deT reaction rate or the hydrogen evolution and deT reaction time (the reaction rate is determined by the size of the initial alloy, then the reaction time is determined) and the reaction effect.
  • the temperature of the alkali solution is T 1 . Therefore, when the reaction rate is used to limit the reaction conditions, the temperature T 1 value and concentration value range of the alkali solution are also indirectly limited.
  • T 1 and concentration C 1 do not need to be specifically limited, but directly
  • the combination of T 1 and C 1 shall be subject to the requirement that the reaction interface proceeds at an average rate of no less than 2 ⁇ m/min during the hydrogen evolution and deT reaction.
  • the average rate of 2 ⁇ m/min is the critical reaction rate at which the initial alloy can undergo nanodisintegration through the hydrogen evolution and deT reaction during the reaction process;
  • the occurrence of nano-fragmentation refers to the fragmentation of the initial alloy through the hydrogen evolution and deT reaction into a single intermediate product or product with at least one dimension in the three-dimensional direction less than 500nm;
  • the occurrence of nano-fragmentation refers to the fragmentation of the initial alloy through the hydrogen evolution and deT reaction into a single intermediate product or product with at least one dimension in the three-dimensional direction less than 250nm;
  • T 1 ⁇ 60°C; further, the T 1 ⁇ 80°C; further, T 1 >100°C;
  • reaction between the initial alloy and the alkali solution is carried out under normal pressure or high pressure
  • reaction between the initial alloy and the alkali solution is carried out in a closed container
  • the initial alloy and the alkali solution are first placed separately in the closed container.
  • the temperature of the alkali solution reaches the set reaction temperature, the initial alloy is contacted with the alkali solution to react.
  • the temperature of the alkali solution can exceed its boiling point temperature under normal pressure
  • the reaction between the initial alloy and the alkali solution is carried out under normal pressure; wherein, the T f solution is the boiling point temperature of the alkali solution participating in the reaction under normal pressure; further , the normal pressure refers to the atmospheric pressure without using a closed container;
  • the reaction is carried out in a normal pressure environment.
  • Normal pressure generally refers to 1 standard atmosphere.
  • the corresponding boiling point of water is 100°C; when alkali is dissolved in water, the boiling point temperature of the aqueous solution of alkali under 1 standard atmosphere. It should be higher than 100°C, and the higher the concentration of alkali, the higher its boiling point.
  • a NaOH solution with a molar concentration of 5 mol/L has a boiling point T f of about 108°C; a NaOH solution with a molar concentration of 7 mol/L has a boiling point T f of about 112°C; a NaOH solution with a molar concentration of 10 mol/L has a boiling point T f
  • the solution is about 119°C; the NaOH solution with molar concentration 12mol/L, the boiling point T f solution is about 128°C; the NaOH solution with molar concentration 15mol/L, the boiling point Tf solution is about 140°C; the NaOH solution with molar concentration 17mol/L , the boiling point T f solution is about 148°C; the molar concentration 20mol/L NaOH solution, the boiling point T f solution is about 160°C; the molar concentration 25mol/L NaOH solution, the boiling point T f solution is about 180°C; the molar concentration 10mol/ L KOH solution, the boiling point
  • the maximum temperature that the reaction solution can be heated to under normal pressure is its boiling point temperature (T f solution )
  • T f solution the maximum temperature that the reaction solution can be heated to under normal pressure
  • the temperature reaches this temperature if the heating continues, the temperature of the solution will not rise and will only boil.
  • the control of the boiling point temperature is the easiest, simplest and most accurate.
  • the reaction time required for the reaction at the boiling point temperature is also shorter than the reaction time required for reactions at other temperatures below the boiling point; the product yield and efficiency are also higher.
  • T-type elements include at least one of Al and Zn, and Al and Zn are amphoteric metals. They can react with alkaline solutions to become salts and thus dissolve in alkaline solutions. Therefore, they can be removed through the reaction of T-type elements and alkaline solutions. T elements in each intermetallic compound in the initial alloy;
  • the characteristic of the hydrogen evolution and T removal reaction is that the T elements in the initial alloy dissolve into the solution and hydrogen gas is precipitated at the same time;
  • the intensity of the hydrogen evolution and deT reaction is related to the reaction advancement rate of the reaction interface from the initial alloy surface inward per unit time. The higher the values of T 1 and C 1 , the faster the reaction interface advancement rate, and the greater the reaction. severe.
  • the reaction interface advances inward from the surface of the initial alloy as follows:
  • the average advancement rate of the reaction interface is about 2 ⁇ m/min to 7 ⁇ m/min;
  • the average advancement rate of the reaction interface is about 7 ⁇ m/min to 15 ⁇ m/min;
  • the average advancement rate of the reaction interface is about 15 ⁇ m/min ⁇ 30 ⁇ m/min;
  • the average advancement rate of the reaction interface is about 30 ⁇ m/min ⁇ 50 ⁇ m/min;
  • the average advancement rate of the reaction interface is about 50 ⁇ m/min ⁇ 120 ⁇ m/min;
  • reaction interface advances inward from the initial alloy surface at an average rate of no less than 7 ⁇ m/min;
  • reaction interface advances inward from the initial alloy surface at an average rate of no less than 15 ⁇ m/min;
  • reaction interface advances inward from the initial alloy surface at an average rate of no less than 30 ⁇ m/min;
  • ultrasonic is applied during the hydrogen evolution and deT reaction, and the nanodisintegration effect and reaction rate are further improved through ultrasonic treatment;
  • the frequency of the ultrasound is 20 kHz to 10 6 kHz;
  • the temperature T 1 of the alkali solution can ensure that the reaction interface advances inward from the initial alloy surface at an average rate of no less than 2 ⁇ m/min during the hydrogen evolution and deT reaction, and During the reaction process, the initial alloy can be nano-disintegrated through the hydrogen evolution and deT reaction. Therefore, under different initial alloy conditions or alkaline solution conditions, when the reaction interface during the hydrogen evolution deT reaction proceeds at no less than 2 ⁇ m/min, the required reaction solution temperature may be lower than 60°C; especially when supplemented by ultrasonic treatment, The required reaction solution temperature may be lower;
  • the Ti element, M-type sub-elements, and D-type sub-elements have different intermediate product evolution and formation trends: specifically,
  • the Ti element has a tendency to generate nano titanate intermediates after shape and composition reconstruction and evolution; further, the Ti-containing intermediate products are mainly nano titanates; further, the shape of the nano titanates is mainly Thin film, with a thickness of 0.5nm-5nm, and an average area of the film greater than 100nm 2 ; further, the cations in the nano titanate correspond to the cations in the alkali solution of the reaction system; for example, the alkali solution of the reaction system is NaOH When , the titanate is sodium titanate;
  • M-type sub-elements have a tendency to generate nano-oxidized M intermediates after shape and composition reconstruction and evolution; further, the M-containing intermediate products are mainly nano-oxidized M; further, the shapes of the nano-oxidized M include film-like , granular, plate-shaped, strip-shaped, tube-rod-shaped, and flocculated at least one; the flocculated shape refers to a state in which extremely small microstructures without obvious edges and corners are agglomerated together. Further, the shape of the nano-oxide M has at least one dimension in the three-dimensional direction not exceeding 500 nm;
  • the nano-oxide M includes at least one of low crystallinity nano-oxide M, crystalline nano-oxide M, and hydrated nano-oxide M; the low-crystallinity nano-oxide M includes amorphous nano-oxide M; Since nanometer hydroxide M can be regarded as a combination of nanometer oxide M and H 2 O, nanometer oxide M can be obtained by heating and dehydration at a lower temperature, so the hydrated nanometer oxide M is nanometer hydroxide M;
  • oxidized Mn can be MnO or MnO 2 ;
  • D-type sub-elements (Zr, Hf elements) have a tendency to dissolve in the alkali solution under the conditions of alkali concentration and temperature corresponding to high reaction rates;
  • D-type sub-elements (Zr, Hf elements) have a tendency to generate D-containing solid substances after shape and composition reconstruction and evolution under alkali concentrations and temperatures corresponding to relatively low reaction rates, and such D-containing solid intermediates include At least one of solid state nanohydrogen D and solid DO 2 ;
  • the high reaction rate is an average reaction rate greater than 15 ⁇ m/min;
  • the relatively low reaction rate is an average reaction rate of less than 15 ⁇ m/min;
  • the shape of the D-containing solid intermediate product has at least one dimension in the three-dimensional direction not exceeding 500 nm;
  • the reaction is carried out under normal pressure and the alkali solution is a hot alkali solution (such as T 1 >100°C), especially when the solution occurs at the boiling point temperature T f of the hot alkali solution, the dissolution phenomenon of the D sub-elements is most obvious.
  • a hot alkali solution such as T 1 >100°C
  • the dissolution of the D-type sub-elements means that a simple D-T intermetallic compound can be dissolved in an alkali solution of a certain temperature and concentration corresponding to a higher reaction rate to obtain a clear and transparent solution; this is the D-type element passing through the D-T intermetallic compound The most unique phenomenon involved in the hydrogen evolution and deT reaction.
  • the evolution and formation trends of the above-mentioned intermediate products are all molar percentages of various sub-elements in the corresponding A-type elements (Ti elements, M-type sub-elements, D-type sub-elements) (see step 1 ) is dominant; when the molar percentage of a certain type of sub-element is not dominant, it may not show the characteristics and trends due to the mutual influence of the intermediate products corresponding to each sub-type element in the formation process. Its evolution and formation trends when it dominates.
  • the term “dominance” refers to the situation where the molar percentage of various sub-elements in the A-type elements (Ti elements, M-type sub-elements, and D-type sub-elements) exceeds 60%. Further, the term “dominance” refers to the situation where the molar percentage of various sub-elements in the A-type elements (Ti elements, M-type sub-elements, and D-type sub-elements) exceeds 75%.
  • the hydrogen evolution and deT reaction of the A-T intermetallic compound will produce a two-dimensional film-like nano-titanate after the shape and composition reconstruction evolution.
  • this in-situ embedding includes in-situ embedding of atoms or atomic clusters (Ti and M are co-existing in nano-titanates, M can be considered a solid solution element), or nano-oxidation of M In-situ embedding of particles.
  • this application not only describes one aspect, but also describes the characteristics of Ti-containing intermediates, M-containing intermediates, and D-containing intermediates generated by the hydrogenation and deTification reaction of A-T intermetallic compounds in several subsequent aspects, all of which are based on the proportion of each component. Characteristics of dominance. When each component does not dominate, it may or may not satisfy the above trends and characteristics. However, if the above trends and characteristics are not met, no matter what the new product is and what its morphology is, it just meets the characteristics of more uniform and thorough recombination, which is conducive to obtaining composite nanometer metal oxides with better performance and Subsequent products.
  • the initial alloy and the alkali solution undergo nano-fragmentation through the hydrogen evolution and deT reaction, and are reconstructed through shape and composition to form a shape with at least one dimension in the three-dimensional direction not exceeding 500nm.
  • the M- and Ti-containing solid material is mainly a composite composed of nano-oxidized M and nano-titanate; the characteristics of the M-containing and Ti-containing solid material are detailed in the evolution and formation trends of each intermediate product mentioned above. describe;
  • the initial alloy contains D sub-elements
  • the initial alloy and the alkali solution undergo nano-fragmentation through a hydrogen evolution and deT reaction, and are reconstructed in shape and composition to form a solid material containing M or/and Ti; at the same time, D
  • the sub-element is mainly dissolved in the alkali solution under the condition of alkali concentration and temperature corresponding to a high reaction rate, or mainly generates D-containing substances through shape and composition reconstruction under the condition of alkali concentration and temperature corresponding to a relatively low reaction rate.
  • Solid substances; the characteristics of the M-containing, Ti-containing, and D-containing solid substances are detailed in the evolution and formation trends of each intermediate product mentioned above;
  • the solid material containing M or/and Ti since in the original AT intermetallic compound, the D-type sub-elements, M-type sub-elements and Ti elements are often evenly distributed in the same phase at the atomic scale, Such as Al 3 (TiZr) phase. Therefore, when the solid matter containing M or (and) Ti is formed, a small number of D-type sub-elements are inevitably restricted in it, so that there are some in the previously formed solid matter containing M or (and) Ti. A small amount of D-type sub-elements participate in the complex; while most D-type sub-elements are dissolved in alkaline solution;
  • the occurrence of nano-fragmentation means that the initial alloy at the reaction interface is fragmented through the hydrogen evolution and deT reaction, and at the same time, the shape and composition are reconstructed to generate nano-scale solid materials containing M or (with) Ti; in this process
  • the violent release of hydrogen promotes the nanofragmentation of intermediates and products, as well as the diffusion distribution of the products in the alkaline solution after leaving the reaction interface.
  • the crushed solid material containing M or (with) Ti does not contain a three-dimensional continuous network-like nano-porous structure or porous skeleton structure;
  • the size of the solid material containing M or (with) Ti is less than 0.25 times the size of the initial alloy before nanodisintegration occurs;
  • the size of the solid material containing M or (with) Ti is less than 0.05 times the size of the initial alloy before nanodisintegration occurs;
  • the thickness or particle size is generally at least a few microns, such as 5 ⁇ m or more; while the particle size or thickness of solid materials containing M or (with) Ti The size does not exceed 500nm, indicating that it has undergone a sufficient nanodisintegration process.
  • the shape reconstruction refers to the nanoscale solid matter containing M or (with) Ti obtained by the hydrogen evolution deT reaction. It is not a simple physical fragmentation of the nanoporous structure (ligament), but occurs in addition to Shape changes beyond physical fragmentation.
  • the approximate shape of the product does not change significantly relative to the initial alloy before and after the reaction; for example, when the initial alloy is granular with edges and corners, the traditional dealloying product generally remains It is in the form of nanoporous particles with the original angular shape; and the shape of the solid material containing M or (with) Ti described in this application is completely different from the shape of the initial alloy, and its shape has undergone great changes;
  • the initial alloy reacts with the alkali solution at a certain temperature and concentration, and the reaction rate is guaranteed to be no less than 2 ⁇ m/min. Solid matter is very important.
  • Comparative Example 1 under normal pressure, when the initial alloy powder containing (NbTi)Al 3 intermetallic compound was reacted with a 10 mol/L NaOH solution at 25°C for 2 hours, the shape of the original alloy powder before and after the reaction was roughly different.
  • the original broken and angular powder particles, and its microstructure does not produce a large number of dispersed products such as nanoparticles, nanosheets or nanorods, but instead produces a nanoporous structure, and this nanoporous structure
  • the structure forms an appearance consistent with the shape of the original alloy powder through three-dimensional network links, and its particle size is still equivalent to the size of the original alloy powder, mainly in the order of several microns or tens of microns.
  • the reaction between the initial alloy and the alkali solution that occurs at a lower temperature near room temperature is completely different from the reaction of the present invention at a higher temperature, such as a temperature range of T 1 >100°C, especially near the boiling point of the alkali solution, and the product form is The appearance is also completely different.
  • the time required for the completion of the hydrogen evolution and deT reaction can be judged by whether the hydrogen evolution is completed. When the gas evolution produced by the reaction cannot be observed with the naked eye, the hydrogen evolution and deT reaction can be considered to be completed.
  • the reaction time for the T elements in the initial alloy to be completely removed through the hydrogen evolution deT reaction is also related to the shape of the initial alloy: when the initial alloy powder particles are smaller, or the initial alloy strips are thinner , the shorter the time required to complete the hydrogen evolution and deT reaction; conversely, the longer the time required to complete the hydrogen evolution and deT reaction.
  • the minimum reaction time t required to complete the hydrogen evolution and deT reaction can be calculated.
  • the initial alloy strip containing the (NbTi)Al 3 intermetallic compound is reacted with a 10 mol/L NaOH solution at the boiling point temperature (the boiling point temperature is about 119°C), and the average reaction interface advancement of the initial alloy strip is The rate is about ⁇ 120 ⁇ m/min, that is, a 40 ⁇ m thick initial alloy strip can complete the hydrogen evolution and deAl reaction in 10 seconds; a 20 ⁇ m thick initial alloy strip can complete the hydrogen evolution and deAl reaction in 5 seconds; even if the initial alloy strip with a 5 mm particle size is For coarse alloy particles, the hydrogen evolution and Al removal reaction can be completed in 21 minutes; considering that the strip or powder particle size may be uneven and there are thicker strips or larger particles, the actual reaction process can be slightly longer to ensure Make sure the initial alloy reaction is complete and proceed to the next step.
  • reaction time of the hydrogen evolution and deTerification is 10s to 59min; further, the reaction time of the hydrogenation and deTelization is 10s to 29min; further, the reaction time of the hydrogenation and deTelization is 10s to 9.9min; further Preferably, the reaction time of the hydrogen evolution and deTermolysis is 10s ⁇ 4.9min; further, the reaction time of the hydrogen evolution and deTermolysis is 10s ⁇ 1min; further, the reaction time of the hydrogen evolution and deTelization is 10s ⁇ 30s;
  • the holding time of the reaction system at the original reaction temperature can still ensure that the product is a nanoscale product with particle dispersion.
  • the morphology of the product may change to a certain extent. That is to say, when the reaction time of the initial alloy and the alkali solution far exceeds the required minimum hydrogen evolution and deT reaction time t, such as up to several hours, a solid material containing M or (and) Ti can still be obtained, but its morphology may Certain changes occur.
  • the initial alloy does not contain D sub-elements, collect the solid materials containing M and Ti in the reaction system to obtain a composite nanometal oxide intermediate product containing M and Ti, the shape of which has at least one shape in the three-dimensional direction.
  • the dimension scale does not exceed 500nm; and the method of compounding the M-containing intermediate product and the Ti-containing intermediate product includes in-situ embedded composite; wherein, the M-containing intermediate product and the Ti-containing intermediate product can be corresponding atoms or atomic clusters, or They may be corresponding phases, and at least one of the M-containing intermediate product and the Ti-containing intermediate product is a phase.
  • the M-containing intermediate product is an atom or an atom cluster, it does not form an M-containing phase, and it exists in the Ti-containing intermediate product phase in the form of atoms or atom clusters.
  • the phase may be a low crystallinity phase or a high crystallinity phase, but it must be a solid phase, such as a low crystallinity hydroxide Zr phase or a high crystallinity oxidation Ta phase; various aspects of this application The explanations related to phase are consistent with this.
  • the process of collecting the solid materials containing M and Ti in the reaction system includes the processes of separation, collection, cleaning and drying of the solid materials containing M and Ti;
  • separation and collection process of solid materials containing M and Ti includes any one of the following a) or b) processes:
  • the cleaning function includes removing the residual alkali on the solid material containing M and Ti, and at the same time cleaning the nanoparticles. Titanates perform cationic adjustments;
  • the hydrogen ion concentration in the dilute acid solution is 0.001 mol/L to 0.1 mol/L;
  • the nano titanate in the solid material containing M and Ti is transformed into nano titanic acid, that is, the nano titanate generates H + and titanate cations replacement, but the shape before and after the transformation is basically unchanged. Further, the shape of the nano titanic acid is a two-dimensional film;
  • composition of the composite nano-metal oxide intermediate product containing M and Ti includes nano-oxide M and at least one of nano-titanate and nano-titanic acid;
  • the thickness of the nano-titanate film is 0.25nm ⁇ 7.5nm; preferably, the thickness of the nano-titanate film is 0.25nm ⁇ 5nm;
  • the thickness of the nano-titanate film is 0.25nm ⁇ 2nm;
  • the average area of the nano-titanate film is greater than 100nm 2 ;
  • the thickness of the nano titanate film is 0.25nm ⁇ 7.5nm; preferably, the thickness of the nano titanate film is 0.25nm ⁇ 5nm;
  • the thickness of the nano titanate film is 0.25nm ⁇ 2nm;
  • the average area of the nano titanate film is greater than 100 nm 2 ;
  • the chemical composition of the nano titanic acid includes H, Ti, and O elements
  • the chemical composition of the nano-titanic acid includes H 4 TiO 4 ;
  • the method of compounding the M-containing intermediate product and the Ti-containing intermediate product includes in-situ embedded compounding and physical adsorption compounding;
  • the M-containing intermediate product is mainly nano-oxidized M
  • the Ti-containing intermediate product is mainly nano-titanate; if it is pickled, the Ti-containing intermediate product is mainly nano-titanic acid;
  • the method of compounding the M-containing intermediate product and the Ti-containing intermediate product includes in-situ embedded composite
  • the in-situ mosaic refers to a formation method of in-situ mosaic generation, that is, the Ti-containing intermediate product and the M-containing intermediate product are combined with each other through part or all of the endogenous mosaic method, without relying on external or external mixing. way to make them distributed among each other; partial endogenous mosaic means that only part of the volume of the embedded component is embedded; it can be understood that when the Ti-containing intermediate product and the M-containing intermediate product are generated at the same time, there must be a Ti-containing intermediate product The product and the M-containing intermediate product are partially or completely embedded in situ with each other;
  • This in-situ intercalation is accomplished simultaneously during the simultaneous formation of Ti-containing intermediates and M-containing intermediates during the hydrogen evolution and deT reaction.
  • the in-situ refers to the simultaneous generation of Ti-containing intermediate products and M-containing intermediate products;
  • This in-situ embedded composite method can ensure that the M-containing intermediate product and the Ti-containing intermediate product are fully and evenly dispersed together during preparation, and the agglomeration of the M-containing intermediate product and the Ti-containing intermediate product will not occur; In comparison, if the M-containing intermediate product and the Ti-containing intermediate product are prepared separately and then mixed, it will be difficult to disperse them uniformly; therefore, in-situ embedded composite cannot occur when the two components are prepared separately and then mixed. situation;
  • M-containing intermediate product and Ti-containing intermediate product can be corresponding atoms or clusters of atoms, or they can be corresponding phases, and at least one of the M-containing intermediate product and the Ti-containing intermediate product is
  • phase means that when the M-containing intermediate is small enough or small enough, it is not enough to form the phase structure of the M-containing intermediate, then it does not exist as a certain phase, but as an M-containing intermediate.
  • Atoms or atomic clusters exist. Although these M-containing atoms or atomic clusters are also combined with O in some way, their size is not large enough to form an oxide phase. However, the composite nanometal oxide intermediate exists as a solid state, which requires at least one phase as a matrix.
  • the Ti-containing intermediate when the M-containing intermediate exists as M-containing atoms or atomic clusters, the Ti-containing intermediate must be used as a matrix. exists in the form of a phase; the phase as a matrix mainly composed of Ti-containing intermediate products can be an amorphous phase, a crystalline phase, or a phase in between; in another case, containing Both the M intermediate product and the Ti-containing intermediate product are corresponding phases. This situation is easy to understand. Which intermediate product has a higher volume percentage is the phase that serves as the matrix.
  • an M-containing intermediate product and a Ti-containing intermediate product are combined into a nearly single structure through in-situ embedded compounding, such as an M/Ti-containing intermediate product, it also falls under the in-situ embedded compounding situation.
  • the M-containing intermediate product and the Ti-containing intermediate product are both M/Ti-containing intermediate products with a certain structure, or even a single phase (at this time, the M-containing intermediate product and the Ti-containing intermediate product are the same M-containing intermediate product.
  • /Ti intermediate and M or (with) Ti is embedded and composited in situ at the atomic scale, which is the most complete composite; in this case, it can be considered that M is embedded in situ in the form of atoms or atomic clusters in M-containing materials.
  • /Ti in the matrix of the intermediate product it can also be considered that Ti is embedded in situ in the matrix of the intermediate product containing M/Ti in the form of atoms or atomic clusters, because the matrix of the intermediate product containing M/Ti is amorphous or low crystalline In the case of the state, it cannot be judged whether the matrix is a Ti-containing intermediate product or an M-containing intermediate product. It can only be considered as an M/Ti-containing intermediate product.
  • the M-containing intermediate product is mainly nano-oxidized M
  • oxidized Mn can be MnO or MnO 2 ;
  • the nano-oxide M includes at least one of low crystallinity nano-oxide M, crystalline nano-oxide M, and hydrated nano-oxide M;
  • the low crystallinity nano-oxide M includes amorphous nano-oxide M
  • nanometer hydroxide M can be regarded as a combination of nanometer oxide M and H 2 O, nanometer oxide M can be obtained by heating and dehydration at a lower temperature, so the hydrated nanometer oxide M is nanometer hydroxide M;
  • nano-oxide M has particle dispersibility
  • the shape of the nano-oxide M has at least one dimension in the three-dimensional direction not exceeding 500 nm;
  • the shape of the nano-oxide M has at least one dimension in the three-dimensional direction not exceeding 250 nm;
  • the shape of the nano-oxide M has at least one dimension in the three-dimensional direction not exceeding 150 nm;
  • the nano-oxide M when the nano-oxide M is in phase, its shape includes at least one of film-like, granular, plate-like, strip-like, tube-rod-like, and flocculated; the flocculated refers to extremely fine and A state in which microstructures without obvious edges and corners are clustered together.
  • nano-oxide M can be softly agglomerated together, they are not closely connected through a three-dimensional continuous rigid network structure and maintain the shape of the original initial alloy.
  • the nano-oxide M is mainly in the form of a film, its thickness is 0.25nm to 30nm; and the average area of the film is greater than 100nm 2 ;
  • the nano-oxide M is mainly in the form of particles, its particle size range is 1.5nm ⁇ 500nm; preferably 1.5nm ⁇ 200nm; preferably 1.5nm ⁇ 100nm;
  • the nano-oxide M when the nano-oxide M is mainly in the form of plates, its thickness ranges from 1.5nm to 100nm, preferably from 5nm to 30nm, and further preferably from 5nm to 20nm; and the average area of the plates is greater than 100nm 2 ;
  • the size of its flocculation microstructure is 1 nm to 15 nm;
  • the nano-oxide M when it is mainly in the shape of a tube or rod, it includes a tube shape or a rod shape, and its diameter ranges from 2 nm to 200 nm; further preferably, it is from 2 nm to 50 nm; and its aspect ratio is greater than 2;
  • the characteristics of the above-mentioned sub-categories of intermediate products are the characteristics and trends displayed when the molar percentages of various sub-elements dominate in the corresponding A-type elements (Ti elements, M-type sub-elements); when a certain When the molar percentage of one type of sub-element is not dominant, due to the mutual influence of the intermediate products corresponding to each sub-type element in the formation process, it may not show the evolution and formation trends when it is dominant.
  • the composite nanometal oxide intermediate product composed of the intermediate product has a shape with at least one dimension in the three-dimensional direction not exceeding 500 nm; and the D-containing intermediate product, the M-containing intermediate product, and the Ti-containing intermediate product are combined with each other in a manner including the original Site-embedded composite; wherein, D-containing intermediate products, M-containing intermediate products, and Ti-containing intermediate products can be corresponding atoms or clusters of atoms, or they can be corresponding phases, and D-containing intermediate products, M-containing intermediate products, and Ti-containing intermediate products At least one of the three intermediate products is a phase.
  • step 2 D-type sub-elements (Zr, Hf elements) have a tendency to generate D-containing solid materials after shape and composition reconstruction and evolution under alkali concentration and temperature corresponding to a relatively low reaction rate, and this kind of D solid intermediate product includes at least one of solid nanohydrogen D and solid DO 2 ;
  • the shape of the D-containing solid intermediate product has at least one dimension in the three-dimensional direction not exceeding 500 nm;
  • the Ti-containing intermediate product is mainly nano-titanate; further, when the nano-titanate is in phase, its shape is mainly film-like, with a thickness of 0.5nm-5nm, and the average area of the film is greater than 100nm. 2 ; Further, the cations in the nano titanate correspond to the cations in the alkali solution of the reaction system; if the alkali solution of the reaction system is NaOH, the titanate is sodium titanate;
  • the M-containing intermediate product is mainly nano-oxidized M; further, when the nano-oxidized M is in phase, its shape includes film, granular, plate, strip, tube-rod, and flocculate. At least one of; the flocculent state refers to a state in which extremely small microstructures without obvious edges and corners are agglomerated together. Further, the shape of the nano-oxide M has at least one dimension in the three-dimensional direction not exceeding 500 nm;
  • the situations in which the intermediate products of each subtype are compounded with each other include any one of the following three types: D-containing intermediate products are compounded with M-containing intermediate products; D-containing intermediate products are compounded with Ti-containing intermediate products, and D-containing intermediate products are compounded. , the M-containing intermediate product and the Ti-containing intermediate product are composited; and the composite method in any of the composite combinations includes in-situ embedded composite;
  • the characteristics of the above-mentioned sub-categories of intermediate products are the characteristics displayed when the molar percentage of each sub-element dominates in the corresponding A-type elements (Ti elements, M-type sub-elements, D-type sub-elements) and trend; when a certain type of sub-element molar percentage does not dominate, due to the mutual influence of the intermediate products corresponding to each sub-type element in the formation process, it may not show the evolution and trend when it is dominant. form a trend.
  • the initial alloy contains D-type sub-elements and the D-type sub-elements are mainly dissolved in the alkali solution
  • concentration that can be precipitated is below C 2
  • the precipitated solid flocculent hydrogenated D is mixed with the previously formed solid matter containing M or (with) Ti, and all solid matter is collected, that is, the nanohydrogenated D and M-containing or (with) Ti are obtained.
  • a composite nano-metal oxide intermediate composed of a solid material of Ti, the shape of which has at least one dimension in the three-dimensional direction not exceeding 500 nm; wherein, when the composite nano-metal oxide intermediate includes an M-containing intermediate and a
  • the method of compounding the M-containing intermediate product with the Ti-containing intermediate product includes in-situ embedded compounding.
  • the M-containing intermediate product and the Ti-containing intermediate product may be corresponding atoms or clusters of atoms, or may be corresponding phases, and at least one of the M-containing intermediate product and the Ti-containing intermediate product is a phase.
  • the liquid is a solvent corresponding to an alkali solution
  • the liquid contains water
  • the temperature of the liquid is normal temperature; further, the temperature of the liquid is 0°C to 40°C;
  • the process of adding liquid is accompanied by sufficient stirring of the alkali solution of the reaction system to ensure that the precipitated solid flocculent hydroxide D adheres to the previously formed M-containing or (with) Ti-containing compounds through heterogeneous nucleation as much as possible.
  • the solid material thereby achieving uniform mixing of hydroxide D and solid material containing M or (with) Ti;
  • concentration of C 2 is determined based on the effect, and its value is the concentration that allows solid flocculent (or colloidal) hydrogen oxide D to precipitate;
  • the precipitation rate of solid flocculent hydrogenated D is controlled; the slower the precipitation of hydrogenated D, the easier it is to react with solid matter containing M or (with) Ti. Mix evenly;
  • the concentration decrease rate does not exceed 0.1mol/L per second
  • the diluted liquid contains surfactant or modifier
  • the purpose of adding surfactants or modifiers to the liquid is to control the particle size of the precipitated nano-oxidized D and inhibit its abnormal merger and growth; further, the surfactants or modifiers include PVP, CTAB, and CTAC. at least one of;
  • the process of collecting all solid substances includes the separation, collection, cleaning and drying processes of all solid substances;
  • the cleaning function includes removing the residual alkali on all solid materials, and at the same time adjusting the cations of the existing nano titanates. , turning it into nano titanate.
  • the nano-titanate in the Ti-containing solid material is transformed into nano-titanic acid, that is, the nano-titanate undergoes replacement of H + with titanate cations.
  • the shape of the nano titanic acid is a two-dimensional film
  • the M-containing intermediate product is mainly nano-oxidized M
  • the Ti-containing intermediate product is mainly nano-titanate; if it is pickled, the Ti-containing intermediate product is mainly nano-titanate;
  • the thickness of the nano-titanate film is 0.25nm ⁇ 7.5nm; preferably, the thickness of the nano-titanate film is 0.25nm ⁇ 5nm;
  • the thickness of the nano-titanate film is 0.25nm ⁇ 2nm;
  • the average area of the nano-titanate film is greater than 100nm 2 ;
  • the thickness of the nano titanate film is 0.25nm ⁇ 7.5nm; preferably, the thickness of the nano titanate film is 0.25nm ⁇ 5nm;
  • the thickness of the nano titanate film is 0.25nm ⁇ 2nm;
  • the average area of the nano titanate film is greater than 500nm 2 ;
  • the chemical composition of the nano titanic acid includes H, Ti, and O elements
  • the chemical composition of the nano-titanic acid includes H 4 TiO 4 ;
  • the composition of the composite nanometer metal oxide intermediate product containing M and Ti includes nanometer oxide M, and simultaneously includes nanometer titanate and nanometer titanate. at least one of;
  • the method of compounding the M-containing intermediate product and the Ti-containing intermediate product includes in-situ embedded composite and physical adsorption composite.
  • the method of compounding the M-containing intermediate product and the Ti-containing intermediate product includes in-situ embedded composite.
  • the method of composite of the nano-oxide M and nano-titanate film includes in-situ embedded composite
  • the method of composite of the nano-oxide M and nano-titanate film includes in-situ embedded composite
  • the nano-oxide M includes at least one of low crystallinity nano-oxide M, crystalline nano-oxide M, and hydrated nano-oxide M;
  • the low crystallinity nano-oxide M includes amorphous nano-oxide M
  • nanometer hydroxide M can be regarded as a combination of nanometer oxide M and H 2 O, nanometer oxide M can be obtained by heating and dehydration at a lower temperature, so the hydrated nanometer oxide M is nanometer hydroxide M;
  • nano-oxide M has particle dispersibility
  • the shape of the nano-oxide M has at least one dimension in the three-dimensional direction not exceeding 500 nm;
  • the shape of the nano-oxide M has at least one dimension in the three-dimensional direction not exceeding 250 nm;
  • the shape of the nano-oxide M has at least one dimension in the three-dimensional direction not exceeding 150 nm;
  • the nano-oxide M when the nano-oxide M is in phase, its shape includes at least one of film-like, granular, plate-like, strip-like, tube-rod-like, and flocculated; the flocculated refers to extremely fine and A state in which microstructures without obvious edges and corners are clustered together.
  • nano-oxide M can be softly agglomerated together, they are not closely connected through a three-dimensional continuous rigid network structure and maintain the shape of the original initial alloy.
  • the nano-oxide M is mainly in the form of a film, its thickness is 0.25nm to 30nm; and the average area of the film is greater than 100nm 2 ;
  • the nano-oxide M is mainly in the form of particles, its particle size range is 1.5nm ⁇ 500nm; preferably 1.5nm ⁇ 200nm; preferably 1.5nm ⁇ 100nm;
  • the nano-oxide M when the nano-oxide M is mainly in the form of plates, its thickness ranges from 1.5nm to 100nm, preferably from 5nm to 30nm, and further preferably from 5nm to 20nm; and the average area of the plates is greater than 100nm 2 ;
  • the size of its flocculation microstructure is 1 nm to 15 nm;
  • the nano-oxide M when it is mainly in the shape of a tube or rod, it includes a tube shape or a rod shape, and its diameter ranges from 2 nm to 200 nm; further preferably, it is from 2 nm to 50 nm; and its aspect ratio is greater than 2;
  • nano-hydroxide D is mainly nano-hydroxide D with low crystallinity
  • the nanohydroxide D has a flocculent structure, and the size range of its flocculent microstructure is 0.5nm to 10nm;
  • the floc-like structure can also be called gel-like structure, or gel-flocculation structure
  • the nanohydrogen D is mainly compounded with the M-containing intermediate product or (with) the Ti-containing intermediate product through physical adsorption recombination. It can be understood that because the precipitation of nanohydroxide D from the solution is later than the formation of M-containing intermediate products or (with) Ti-containing intermediate products, therefore, it mainly interacts with M-containing intermediate products or (with) Ti-containing intermediate products through physical adsorption. Compounding of intermediate products;
  • nano-hydroxide D is mainly compounded with the nano-oxide M or (with) the nano-titanate film through physical adsorption;
  • the characteristics of the above-mentioned sub-categories of intermediate products are the characteristics displayed when the molar percentage of each sub-element dominates in the corresponding A-type elements (Ti elements, M-type sub-elements, D-type sub-elements) and trend; when a certain type of sub-element molar percentage does not dominate, due to the mutual influence of the intermediate products corresponding to each sub-type element in the formation process, it may not show the evolution and trend when it is dominant. form a trend.
  • thermal stability or (and) crystallization temperature of the composite nanometer metal oxide intermediate product is higher than the thermal stability or (and) crystallization temperature of the corresponding single nanometer metal oxide intermediate product prepared by a similar process.
  • This increase in thermal stability or/or crystallization temperature is related to the special combination of different A-type sub-elements (element Ti, M-type sub-elements, D-type sub-elements) in the composite nano-metal oxide intermediate.
  • This kind of composite that improves thermal stability or (and) crystallization temperature includes two types: one is the initial in-situ embedded composite, including in-situ embedded composite of atoms, atomic clusters, and phase scales; the other is nano-hydrogen oxidation D uses ultra-fine, ultra-highly dispersed physical adsorption and compounding of other intermediate products, which will induce a sintered embedded compound during the later heat treatment process. For example, when ultrafine flocculent hydrogen oxide D is precipitated, it is uniformly adsorbed on the previously precipitated nanometer oxide M.
  • the two are initially physically adsorbed and combined, due to this physical adsorption is extremely uniform and the scale is extremely small, in the subsequent During the sintering process, heat treatment will induce a state of sintered embedded composite, causing smaller atoms or phases to be wrapped by the matrix phase after sintering.
  • the existence of this sintered embedded composite will affect the volume of the main matrix phase.
  • the atoms in the material are diffusely rearranged, thereby improving the thermal stability or (and) crystallization temperature during the sintering process.
  • the combination of dissimilar components at extremely small scales will affect the diffusion rearrangement of matrix phase atoms, thereby improving the thermal stability or (and) crystallization temperature of the composite nanometal oxide intermediate.
  • the thermal stability or crystallization temperature of composite nanometal oxide intermediates composed of Ti elements and M-type sub-elements is higher than that of nanometal oxide intermediates composed of Ti elements alone or M-type elements alone. properties or crystallization temperature.
  • the composite nanometer metal oxide intermediate product contains at least two of the three types of sub-elements: element Ti, M-type sub-elements, and D-type sub-elements; and the composite nanometer metal oxide intermediate product, At least two of the three types of sub-elements, Ti element, M-type sub-element, and D-type sub-element, are at the atomic/atom cluster scale or fine phase (abbreviation for fine phase) scale where heterogeneous elements correspond to oxide intermediates.
  • the composite wherein the atom/atom cluster scale size is 0.25nm-2.5nm; the average particle size of the fine phase is less than 250nm;
  • At least two types of sub-elements among the three types of sub-elements: Ti element, M-type sub-elements, and D-type sub-elements are processed at the atomic/atom cluster scale or the fine phase scale.
  • the initial alloy contains D-type sub-elements
  • the D-type sub-elements are mainly dissolved in the alkali solution at the alkali concentration and temperature corresponding to the high reaction rate
  • the D-type sub-elements will be reduced after the alkali solution concentration is reduced.
  • the sub-element is mainly precipitated through hydroxidation of D, and is mainly combined with the previously precipitated M-containing intermediate product or (with) Ti-containing intermediate product by physical adsorption.
  • the method of compounding the M-containing intermediate product with the Ti-containing intermediate product includes in-situ embedded compounding.
  • the average particle size of the fine phase of the intermediate product is lower than 125 nm; further, the average particle size of the fine phase of the intermediate product is lower than 50 nm;
  • the average particle size of the fine phase of the intermediate product is lower than 25 nm; further, the average particle size of the fine phase of the intermediate product is lower than 15 nm;
  • the atom/atom cluster scale is 0.25nm-2.5nm; the atomic scale is 0.25nm-0.5nm, and the atomic cluster scale is 0.5nm-2.5nm; the 0.25nm-2.5nm scale is not enough to form an intermediate product phase, It can only be called atoms or clusters of atoms;
  • the three types of elements, Ti element, M-type sub-elements, and D-type sub-elements are combined with heterogeneous elements at the atomic/atom cluster scale; wherein, the atom/atom cluster The scale size is 0.25nm-2.5nm.
  • the temperature of the heat treatment is 300°C to 2000°C; further, the temperature of the heat treatment is 400°C to 2000°C; further, the temperature of the heat treatment is 500°C to 2000°C;
  • the heat treatment time is 1min ⁇ 24h; further, the heat treatment time is 5min ⁇ 24h;
  • the heat treatment time is 30min ⁇ 24h
  • the three types of elements Ti element, M-type sub-elements, and D-type sub-elements, are present at the atomic/atom cluster scale or fine phase (abbreviation for fine phase).
  • the scale is used to perform the compounding of heterogeneous elements; wherein the scale size of the atom/atom cluster is 0.25nm-2.5nm; the average particle size of the fine phase is less than 250nm;
  • phase corresponding to the Ti element is partially crystallized or fully crystallized nano-TiO 2 ;
  • phase corresponding to the M-type sub-element is partially crystallized or fully crystallized nano-oxide M, the D-type sub-element
  • the phase corresponding to the element is partially crystallized or fully crystallized nano-DO 2 ;
  • the average particle size of the fine phase is lower than 125 nm; further, the average particle size of the fine phase is lower than 50 nm;
  • the average particle size of the fine phase is lower than 25 nm; further, the average particle size of the fine phase is lower than 15 nm;
  • the atom/atom cluster scale is 0.25nm-2.5nm; the atomic scale is 0.25nm-0.5nm, and the atomic cluster scale is 0.5nm-2.5nm; at the 0.25nm-2.5nm scale, it is not enough to form a phase and can only Called atoms or clusters of atoms;
  • the three types of elements, Ti element, M-type sub-elements, and D-type sub-elements are combined with heterogeneous elements at the atomic/atomic cluster scale; wherein, the atoms /The size of the atomic cluster is 0.25nm-2.5nm.
  • the degree of crystallization of the phase corresponding to each sub-type of A-type elements is related to the heat treatment temperature and time; according to the phase transformation law, when crystallization is incomplete, partially crystallized nano-TiO 2 may contain titanic acid components.
  • Partially crystallized nanometer DO 2 may contain the component hydroxide M; partially crystallized nanometer DO 2 may contain the component hydroxide D.
  • the three types of elements are compounded of heterogeneous elements at the atomic/atomic cluster scale or fine phase scale; wherein , the scale size of the atoms/atom clusters is 0.25nm-2.5nm; the average particle size of the fine phase is less than 250nm
  • the Ti element, M type The corresponding components of sub-elements and D-type sub-elements are judged separately.
  • the particle size of the smaller components is either at the atomic/atom cluster level (0.25nm-2.5nm), or the average particle size is less than 250nm. Fine phase level.
  • the composite nanometal oxide with increased crystallization is (TiCr)O 2 , which is formed by inserting a small amount of Cr into TiO 2 with atoms or atomic clusters, then the Ti element and Cr element (belonging to the M-type sub-elements) are The composite of heterogeneous elements is carried out at the atomic/atom cluster scale; if the composite nanometal oxide with an increased degree of crystallization is the ZrO 2 phase and is composited with the Cr oxide phase, then the average particle size of the smaller phase between the two is Fine phase level below 250nm and above 2.5nm. That is, the expression of fine phase is the situation where two or more phases appear, and the fine phase is the phase with smaller average size. (This explanation applies to all aspects of this application, including aspects one to four)
  • the composite nano-metal oxide with an increased degree of crystallization when the three types of elements, Ti element, M-type sub-elements, and D-type sub-elements, are combined with heterogeneous elements at the fine phase scale, the composite nano-metal oxide
  • the evolution rules and product characteristics during the heat treatment process include the following characteristics:
  • the composite nanometal oxide is mainly a composite of nanometer oxide M and nanometer TiO 2 ; and the method of composite of the nanometer oxide M and nanometer TiO 2 includes in-situ embedded composite ;
  • the composite nanometal oxide is mainly a composite of nanometer DO 2 and nanometer oxide M or (with) nanometer TiO 2 ; and when the composite nanometer metal oxide also includes nanometer
  • the composite method of nano-oxidizing M and nano-TiO 2 includes in-situ embedded composite.
  • the composite of nano-DO 2 and nano-oxide M or (with) nano-TiO 2 includes three situations: the composite of nano-DO 2 and nano-oxide M; the composite of nano-DO 2 and nano-TiO 2 ; nano-DO 2 Composite with nano-oxide M and nano-TiO 2 ;
  • oxidized Mn can be MnO or MnO 2 ;
  • the nano-titanic acid in the composite nano-metal oxide intermediate product gradually transforms into anatase TiO 2 and then further into rutile type TiO 2 transformation;
  • the nano-hydroxide D in the composite nano-metal oxide intermediate product gradually transforms into crystalline nano-DO 2; wherein, the crystalline nano-DO 2 State DO 2 includes at least one of three situations: ZrO 2 , HfO 2 , (Zr/Hf)O 2 ;
  • the transformation degree of the composite nano-metal oxide intermediate product in the above three cases a)-c) is related to the heat treatment time and temperature. Under certain heat treatment time and temperature conditions, products with any degree of crystallization (crystallinity 0-100%) are within the scope of protection of this application; as long as the heat treatment time is long enough and the temperature is high enough, the composite nano-metal oxide intermediate product The above-mentioned transformations a)-c) can all occur completely.
  • the evolution trends and characteristics of the above-mentioned sub-categories of intermediate products during the heat treatment process are all molar percentages of various sub-elements in the corresponding A-type elements (Ti elements, M-type sub-elements, D-type sub-elements) Characteristics and trends displayed when the elements are dominant; when the molar percentage of a certain sub-element is not dominant, due to the mutual influence of the evolution trends and characteristics of the intermediate products corresponding to each sub-element during the heat treatment process, it may It does not show the evolutionary trends and characteristics when it dominates.
  • the composite nano-metal oxide intermediate product is originally in an in-situ embedded state, such as the in-situ embedded composite of nano-M oxide and nano-titanic acid, which is in the best and uniformly dispersed state before sintering, it will still remain in the state after sintering.
  • the best uniform dispersion state can be obtained;
  • the particle porosity or (and) specific surface area of the composite nanometal oxide is higher than the particle porosity or (and) specific surface area of the corresponding single nanometal oxide prepared by a similar process.
  • the reasons for this phenomenon are similar to the reasons for the thermal stability of the composite nanometal oxide intermediate product or (and) the increase in crystallization temperature, and are related to the initial in-situ embedded composite or the sintering embedded composite induced by heat treatment.
  • Finer particles of composite nanometal oxides with an increased degree of crystallization for example, a single flocculent Zr hydroxide intermediate product, which is obtained by heat treatment to obtain crystalline ZrO 2 , the crystalline ZrO 2 is often sintered into an extremely dense block Large particles have little shrinkage inside, so it is difficult to break them through subsequent sand grinding and ball milling processes to obtain finer crystalline ZrO 2 ; and when the flocculent hydrogenation Zr intermediate product is compounded with other materials containing Ti and Nb component, it not only increases the temperature of its complete crystallization, but also can obtain loose, high specific surface area composite nano-metal oxide particles through heat treatment, which are mainly composed of crystalline ZrO 2 and are compounded with Ti-containing and Nb-containing The particles with this structure can easily obtain finer composite nano-metal oxide particles through subsequent sand grinding and ball milling. See Example 1 and Comparative Example 2.
  • the nano titanate film has a tendency to evolve into flake crystalline nano TiO 2 after heat treatment
  • the thickness of the crystalline nano-TiO 2 sheets is 2 nm to 20 nm; the average area of the crystalline nano-TiO 2 sheets is greater than 100 nm 2 ;
  • phase composition of the flake crystalline nano-TiO 2 in the composite nano-metal oxide includes at least one of brookite-type TiO 2 , nano-anatase nano-TiO 2 , and rutile-type nano-TiO 2 .
  • flocculent nanohydroxide D has a tendency to evolve into granular crystalline nanometer DO 2 after heat treatment
  • the particle size of the crystalline nano-DO 2 is 3 nm to 500 nm;
  • the nano-oxidized M has a tendency to evolve into crystalline nano-oxidized M after heat treatment; its shape includes at least one of film, granular, plate, strip, tube and rod, and sintered agglomerate;
  • the shape of the crystalline nanooxide M is a film
  • its thickness is 2 nm to 20 nm; more preferably, it is 3 nm to 10 nm; the average area of the film is greater than 200 nm 2 ;
  • the shape of the crystalline nanooxide M is granular, its particle size ranges from 3 nm to 500 nm;
  • the shape of the crystalline nanooxide M is plate-like, its thickness is 6 nm to 75 nm, and the average area of the plate is greater than 30 nm 2 ;
  • the shape of the crystalline nanooxide M is a strip, its diameter ranges from 3 nm to 60 nm, and the aspect ratio is greater than 4;
  • the shape of the crystalline nanooxide M is a tube-rod shape, it includes a tube shape and a rod shape, its diameter ranges from 3 nm to 200 nm, and its aspect ratio is greater than 2;
  • the shape of the crystalline nano-oxide M is sintered agglomeration, its particle size increases significantly due to sintering agglomeration, and the particle size range is 5 nm to 1 mm;
  • the characteristics of the above-mentioned sub-categories of intermediate products are the characteristics displayed when the molar percentage of each sub-element dominates in the corresponding A-type elements (Ti elements, M-type sub-elements, D-type sub-elements) and trend; when a certain type of sub-element molar percentage does not dominate, due to the mutual influence of the intermediate products corresponding to each sub-type element in the formation process, it may not show the evolution and trend when it is dominant. form a trend.
  • the composite nano-metal oxide with an increased degree of crystallization contains at least two of the three sub-elements: Ti, M-type sub-elements, and D-type sub-elements; and the composite nano-metal oxide has , at least two types of sub-elements among the three types of sub-elements: Ti element, M-type sub-elements, and D-type sub-elements, perform the corresponding oxides of heterogeneous elements at the scale of atoms/atom clusters or fine phases (abbreviation for fine phases).
  • Composite wherein the atom/atom cluster size is 0.25nm-2.5nm; the average particle size of the fine phase is less than 250nm;
  • At least two types of sub-elements among the three types of sub-elements: Ti element, M-type sub-elements, and D-type sub-elements are dissimilar elements at the atomic/atom cluster scale or the fine phase scale.
  • In-situ embedded composite of corresponding oxides are dissimilar elements at the atomic/atom cluster scale or the fine phase scale.
  • the "oxides corresponding to heterogeneous elements” refer to the oxides formed when there are at least two types of sub-elements among the three types of sub-elements: Ti element, M-type sub-elements, and D-type sub-elements in the composite nano-metal oxide.
  • Ti element Ti element
  • M-type sub-elements M-type sub-elements
  • D-type sub-elements in the composite nano-metal oxide.
  • the nanooxide Ti it is considered that there are at least two types of nanooxide Ti, nanooxide M, and nanooxide D.
  • the nano-oxide Ti phase, nano-oxide M phase, or nano-oxide D phase may not actually be found in the composite nano-metal oxide.
  • a certain type of sub-type elements may be solid dissolved in the oxides of other types of sub-elements, or heterogeneous sub-type elements may be combined into a new multi-component oxide.
  • Ti is solidly dissolved in Zr oxide
  • the composite nanometal oxide only exhibits the crystal structure of Zr oxide
  • this application still considers the composite nanometal oxide to be a composite of Ti oxide and Zr oxide.
  • the composite nanometal oxide is a single-phase Ti/Nb oxide, which does not exhibit the crystal structure of Ti oxide, nor does it exhibit the crystal structure of Nb oxide, but exhibits a new crystal structure, then this application also considers that this The composite nanometal oxide is a composite of Ti oxide and Nb oxide.
  • Ti does not exist as a separate oxidized Ti phase, so Ti is a composite of corresponding oxides of heterogeneous elements at the atomic/atom cluster scale.
  • the special composite of the composite nanometal oxide prepared in this application is achieved, which is of positive significance. (This interpretation applies to all aspects of this application, including similar situations from aspects one to four)
  • a method for preparing a composite nanometal oxide intermediate product includes the following steps:
  • Step 1 the process is completely consistent with the process described in step 1 on the one hand, see the description on the other hand for details;
  • Step 2 the process is completely consistent with the process described in Step 2 on the one hand, see the details on the other hand;
  • Step 3 the process is completely consistent with the process described in Step 3 on the one hand, see the details on the other hand;
  • steps 1 to 3 of the second aspect are completely the same as the steps 1 to 3 of the first aspect, including detailed descriptions of each sub-step. For details, see the description of steps 1 to 3 of the first aspect and will not be repeated here.
  • a method for preparing composite nanometal oxides includes the following steps:
  • Step (1) provide an initial alloy, the composition of the initial alloy includes T-type elements and A-type elements, wherein the T-type elements include at least one of Al and Zn; the A-type elements include elements Ti and M-type sub-elements , D-type sub-elements, at least two of the three types of sub-elements; among them, M-type sub-elements include Cr, V, Nb, Ta, W, Mo, Mn, Y, La, Ce, Pr, Nd, Pm, Sm , at least one of Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu; the D sub-elements include at least one of Zr and Hf; the composition of the initial alloy is mainly A x T y , where x and y are the atomic percentage contents of the corresponding elements, and 5 ⁇ x ⁇ 55%, 45% ⁇ y ⁇ 95%; the solidification structure of the initial alloy is mainly composed of AT intermetallic compounds;
  • Step (2) mix the initial alloy with an alkali solution with a temperature of T 1 and a concentration of C 1 ; wherein, T s solution ⁇ T 1 ⁇ T f solution , and T f solution is the reaction solution under normal pressure.
  • the boiling point temperature of the alkali solution; T s solution is the freezing point temperature of the alkali solution participating in the reaction under normal pressure;
  • Step (3) mix the solid material obtained in step (2) with an alkali solution with a concentration of C2 , then place the mixture in a closed container, and then treat it at a temperature T2 higher than normal pressure for a period of time, where T 2 >T f solution ;
  • Step (4) after cooling down the temperature and pressure
  • the initial alloy does not contain D sub-elements, collect the solid matter in the reaction system to obtain a composite nanometal oxide intermediate product containing M and Ti, whose shape has at least one dimension in the three-dimensional direction not exceeding 500nm; And the method of compounding the M-containing intermediate product and the Ti-containing intermediate product includes in-situ embedded composite; wherein, the M-containing intermediate product and the Ti-containing intermediate product can be corresponding atoms or atomic clusters, or they can be corresponding phases, and At least one of the M-containing intermediate product and the Ti-containing intermediate product is a phase;
  • the liquid is added to the reaction system after cooling and pressure reduction, so that the concentration of the diluted alkali solution C 3 ⁇ 3mol/L, and all solid materials are collected, that is, the mixture of D-containing solid materials and A composite nano-metal oxide intermediate product composed of a solid material containing M or (with) Ti, the shape of which has at least one dimension in the three-dimensional direction not exceeding 500 nm; wherein, C 3 ⁇ C 2 ; and when the composite nano-metal
  • the oxide intermediate product includes both an M-containing intermediate product and a Ti-containing intermediate product, the method of compounding the M-containing intermediate product and the Ti-containing intermediate product includes in-situ embedded compound; wherein, the M-containing intermediate product and the Ti-containing intermediate product can be The corresponding atoms or atom clusters can also be corresponding phases, and at least one of the M-containing intermediate product and the Ti-containing intermediate product is a phase;
  • Step (5) heat-treat the composite nano-metal oxide intermediate product described in step (4) to obtain a composite nano-metal oxide with an increased degree of crystallization; which includes the elements Ti, M-type sub-elements, and D-type sub-elements. At least two of the three types of sub-elements; and at least two of the three types of sub-elements, Ti elements, M-type sub-elements, and D-type sub-elements, correspond to heterogeneous elements at the atomic/atom cluster scale or fine phase scale. compound of oxides.
  • the alkali solution includes at least one of NaOH, KOH, LiOH, RbOH, CsOH, Ba(OH) 2 , Ca(OH) 2 , and Sr(OH) 2 solutions;
  • the solvent in the alkaline solution contains water; preferably, the solvent in the alkaline solution is water;
  • the concentration C 1 of the alkali in the alkali solution is 0.5 mol/L ⁇ 30 mol/L; further, the concentration C 1 of the alkali in the alkali solution is 1 mol/L ⁇ 30 mol/L; preferably, the The alkali concentration C 1 in the alkali solution is 5 mol/L to 15 mol/L; since the subsequent step (3) includes a reaction at high temperature and high pressure, the low value of the alkali solution concentration C 1 range can be as low as 0.5 mol/L. At this concentration, combined with high temperature and high pressure conditions, the corresponding target reaction can also be achieved.
  • the alkali in the alkali solution mixed with the initial alloy is an excessive dose, and the number of moles of the alkali is more than 5 times the number of moles of the initial alloy; further, the number of moles of the alkali is more than 10 times the number of moles of the initial alloy; Further, the number of moles of base is more than 20 times the number of moles of initial alloy;
  • step two When the initial alloy is mixed with an alkali solution with a temperature of T 1 and a concentration of C 1 , and the reaction interface advances inward from the surface of the initial alloy at an average rate of not less than 2 ⁇ m/min during the hydrogen evolution and deT reaction, it is On the one hand, the situation described in step two is shown in step two on the other hand for details.
  • the step (2) includes one aspect of the step The situation described in the second aspect, that is, after the situation described in step two on the one hand, the subsequent step (3) is performed, which still falls within the protection scope of the three aspects of this application.
  • step (3) When there is a subsequent step (3), whether nanodisintegration occurs or not, or whether the hydrogen evolution and deT reaction is completed after the initial alloy is mixed with the alkali solution in step (2), it is not necessary for the step (2).
  • the reaction results have a fundamental impact. Because the reaction in step (3) is carried out for a longer time, at a higher temperature, especially at a higher pressure, regardless of the values of temperature T 1 and concentration C 1 in step (2), or regardless of the results obtained in step (2) Regardless of the intermediate product, the characteristics of its reactants or intermediate products will be covered by subsequent processes, and a new reaction equilibrium will be reached in step (3), while the final product under this equilibrium condition will be obtained.
  • the reaction interface is formed from the initial alloy at an average rate of less than 2 ⁇ m/min during the hydrogen evolution and deT reaction.
  • the solid material obtained in step (2) is mixed with an alkali solution with a concentration of C2 , and then the mixture is placed in a closed container.
  • the specific operation process includes at least one of the following two schemes:
  • step (2) Directly place the solid material obtained in step (2) and the alkali solution mixture with a concentration of C 1 in a closed container; at this time, there is no need to increase or decrease the alkali solution, and C 2 ⁇ C 1 , the concentrations of C 2 and C 1 The slight difference comes from the consumption of a small amount of alkali due to the hydrogen evolution and deT reaction in step (2);
  • step (2) First separate the solid material obtained in step (2) from the alkali solution with a concentration of C1 , then mix it with the alkali solution with a concentration of C2 and place it in a closed container; at this time, the alkali solution with a concentration of C2 and the alkali solution with a concentration of C2
  • concentration and alkali type of the alkali solution with a concentration of C 1 may be the same, or they may not be consistent with the concentration and alkali type of the alkali solution with a concentration of C 1 ;
  • the range of C 2 is 0.5 mol/L ⁇ 30 mol/L; further, the range of C 2 is 1 mol/L ⁇ 30 mol/L; further, the range of C 2 is 5 mol/L ⁇ 30mol/L;
  • the pressure is higher than normal pressure but lower than 100MPa; further, the pressure is higher than normal pressure but lower than 20MPa;
  • T f solution ⁇ T 2 ⁇ 500°C; further, T f solution ⁇ T 2 ⁇ 300°C;
  • the processing time at T 2 temperature higher than normal pressure is 1mim ⁇ 48h; further, the processing time at T 2 temperature higher than normal pressure is 1mim ⁇ 12h; further, the processing time at T 2 temperature higher than normal pressure is 1mim ⁇ 12h;
  • the treatment time at T2 temperature at normal pressure is 1mim ⁇ 2h; further, the treatment time at T2 temperature higher than normal pressure is 1mim ⁇ 30mim; further, the treatment time at T2 temperature higher than normal pressure is It is 1mim ⁇ 10min;
  • the processing time at T 2 temperature higher than normal pressure is related to the concentration of C 2 , the pressure, and the size of T 2 ; the higher the concentration of C 2 , the greater the pressure, and the higher T 2 , then The shorter the reaction time required.
  • concentration of C 2 takes a low value in its range, such as 0.5mol/L, and the solvent is water, it is a common condition for hydrothermal reaction, and a low-concentration alkali is a mineralizer under hydrothermal reaction conditions;
  • the treatment time at T 2 temperature higher than normal pressure is 1mim ⁇ 2h;
  • the treatment time at T 2 temperature higher than normal pressure is 1mim ⁇ 30mim
  • the treatment time at T 2 temperature higher than normal pressure is 30mim ⁇ 48h;
  • the temperature reduction is to a temperature below 100°C; further, the temperature reduction is to a temperature below 50°C;
  • the initial alloy does not contain D sub-elements, collect the solid matter in the reaction system to obtain a composite nanometal oxide intermediate product containing M and Ti, whose shape has at least one dimension in the three-dimensional direction not exceeding 500nm; And the method of compounding the M-containing intermediate product and the Ti-containing intermediate product includes in-situ embedded composite; wherein, the M-containing intermediate product and the Ti-containing intermediate product can be corresponding atoms or atomic clusters, or they can be corresponding phases, and At least one of the M-containing intermediate product and the Ti-containing intermediate product is a phase;
  • the shape of the Ti-containing intermediate product includes at least one of film, tube, rod, and fiber;
  • the shape of the Ti-containing intermediate product includes at least one of tubular, rod-shaped, and fibrous;
  • the process of collecting solid matter in the reaction system includes the separation, collection, cleaning and drying processes of the composite nanometal oxide intermediate product containing M and Ti;
  • the residual alkali on the intermediate product is simultaneously adjusted to the cationic state of the nanotitanate.
  • the hydrogen ion concentration in the dilute acid solution is 0.001 mol/L to 0.1 mol/L;
  • the M-containing intermediate product is mainly nano-oxidized M
  • the Ti-containing intermediate product is mainly nano titanate
  • the nano-titanate in the composite nano-metal oxide intermediate product containing M and Ti is converted into nano-titanium acid, that is, nano-titanium
  • the acid salt undergoes replacement of H + with titanate cations.
  • the shape of the nano-titanate includes at least one of film, tube, rod, and fiber;
  • the Ti-containing intermediate product is mainly nano titanic acid
  • composition of the composite nano-metal oxide intermediate product containing M and Ti includes nano-oxide M and at least one of nano-titanate and nano-titanic acid;
  • the shape of the nano-titanate includes at least one of tubular, rod-shaped, and fiber-shaped; and its cross-sectional diameter is 2nm-20nm;
  • the shape of the nano-titanic acid includes at least one of tubular, rod-shaped, and fiber-shaped; and its cross-sectional diameter is 2nm-20nm;
  • the method of compounding the M-containing intermediate product and the Ti-containing intermediate product includes in-situ embedded compounding; the characteristics and explanation of the in-situ embedded compounding have been described on the one hand, see the first aspect; here and the first aspect thereof The only difference is: on the one hand, the Ti-containing intermediate product is mainly in the form of a film, while the shape of the Ti-containing intermediate product here includes at least one of film, tube, rod, and fiber;
  • the method of compounding the M-containing intermediate product and the Ti-containing intermediate product includes in-situ embedded composite
  • the method of compounding the M-containing intermediate product and the Ti-containing intermediate product includes in-situ embedded composite, and when the M-containing intermediate product and the Ti-containing intermediate product are combined into something close to a single structure, such as M/Ti-containing When it is an intermediate product, it also belongs to this in-situ embedded compound situation.
  • both the M-containing intermediate product and the Ti-containing intermediate product are M/Ti-containing intermediate products with a certain structure, and M and Ti are embedded and recombined in situ at the atomic scale, which is the most complete recombination.
  • the method of composite of the nano-oxide M and nano-titanate includes in-situ embedded composite
  • the method of composite of the nano-oxidized M and nano-titanic acid includes in-situ embedded composite
  • the nano-oxide M includes at least one of low crystallinity nano-oxide M, crystalline nano-oxide M, and hydrated nano-oxide M;
  • the low crystallinity nano-oxide M includes amorphous nano-oxide M
  • nanometer hydroxide M can be regarded as a combination of nanometer oxide M and H 2 O, nanometer oxide M can be obtained by heating and dehydration at a lower temperature, so the hydrated nanometer oxide M is nanometer hydroxide M;
  • nano-oxide M has particle dispersibility
  • oxidized Mn can be MnO or MnO 2 ;
  • the shape of the nano-oxide M has at least one dimension in the three-dimensional direction not exceeding 500 nm;
  • the shape of the nano-oxide M has at least one dimension in the three-dimensional direction not exceeding 250 nm;
  • the shape of the nano-oxide M has at least one dimension in the three-dimensional direction not exceeding 150 nm;
  • the shape of the nano-oxide M includes at least one of film, granular, plate, strip, tube-rod, and floc; the floc refers to extremely small and without obvious edges and corners. The state in which microstructures are clustered together.
  • nano-oxide M can be softly agglomerated together, they are not closely connected through a three-dimensional continuous rigid network structure and maintain the shape of the original initial alloy.
  • the nano-oxide M is mainly in the form of a film, its thickness is 0.25nm to 30nm; and the average area of the film is greater than 100nm 2 ;
  • the nano-oxide M is mainly in the form of particles, its particle size range is 1.5nm ⁇ 500nm; preferably 1.5nm ⁇ 200nm; preferably 1.5nm ⁇ 100nm;
  • the nano-oxide M when the nano-oxide M is mainly in the form of plates, its thickness ranges from 1.5nm to 100nm, preferably from 5nm to 30nm, and further preferably from 5nm to 20nm; and the average area of the plates is greater than 100nm 2 ;
  • the size of its flocculation microstructure is 1 nm to 15 nm;
  • the nano-oxide M when it is mainly in the shape of a tube or rod, it includes a tube shape or a rod shape, and its diameter ranges from 2 nm to 200 nm; further preferably, it is from 2 nm to 50 nm; and its aspect ratio is greater than 2;
  • the liquid is added to the reaction system after cooling and pressure reduction, so that the concentration of the diluted alkali solution C 3 ⁇ 3mol/L, and all solid materials are collected, that is, the mixture of D-containing solid materials and A composite nano-metal oxide intermediate product composed of a solid material containing M or (with) Ti, the shape of which has at least one dimension in the three-dimensional direction not exceeding 500 nm; wherein, C 3 ⁇ C 2 , and when the composite nano-metal
  • the oxide intermediate product includes both an M-containing intermediate product and a Ti-containing intermediate product
  • the method of compounding the M-containing intermediate product and the Ti-containing intermediate product includes in-situ embedded compound; wherein, the M-containing intermediate product and the Ti-containing intermediate product can be
  • the corresponding atoms or atom clusters may also be corresponding phases, and at least one of the M-containing intermediate product and the Ti-containing intermediate product is a phase.
  • the shape of the Ti-containing intermediate product includes at least one of film, tube, rod, and fiber;
  • the liquid includes water
  • the temperature of the liquid is normal temperature; further, the temperature of the liquid is 0°C to 40°C;
  • the concentration of the alkali solution is reduced to below C3 .
  • the D-type sub-elements have been dissolved in the C2 alkali solution before dilution, by adjusting the concentration value of C3 , the D-type elements can be flocculated in the diluted alkali solution.
  • the D-type elements are not dissolved and are already solid before dilution, precipitation of D hydroxide will not occur at this time.
  • C 2 is in the high value area of its range, such as 7-30mol/L, and the D-type elements are dissolved in the alkali solution; after dilution, the D-type elements are oxidized with flocculent hydrogen in the diluted alkali solution.
  • Precipitate in the form of D further, the nano-hydroxide D is mainly nano-hydroxide D with low crystallinity; further, the nano-hydroxide D has a flocculent structure, and the size range of its flocculent microstructure is 0.5nm ⁇ 10nm;
  • C 2 is in the low value area of its range, such as 0.5-3mol/L.
  • the D-type elements have become solid nano-DO 2 through high-temperature and high-pressure hydrothermal reactions. Among them, the effect of lower concentration alkali It is a mineralizer; after dilution, solid nano-DO 2 is still retained;
  • the particle size of the nano-DO 2 is 3 nm to 500 nm;
  • C 2 is in the mid-range of its range, such as 3-7 mol/L, and the evolution law of D-type elements is between the above two; that is, after dilution, D-containing products including solid nano-DO 2 are obtained With flocculent hydrogen oxidation D;
  • the diluted liquid contains surfactant or modifier
  • the purpose of adding surfactants or modifiers to the liquid is to control the particle size of the precipitated nano-oxidized D and inhibit their abnormal merger and growth; further, the surfactants or modifiers include at least one of PVP, CTAB, and CTAC. A sort of;
  • the process of collecting all solid substances includes the separation, collection, cleaning and drying processes of all solid substances;
  • the cleaning function includes removing the residual alkali on all solid materials, and at the same time adjusting the cations of the existing nano titanates. .
  • the nano-titanate in the Ti-containing solid material is transformed into nano-titanic acid, that is, the nano-titanate undergoes replacement of H + with titanate cations.
  • the hydrogen ion concentration in the dilute acid solution is 0.0001 mol/L to 0.09 mol/L;
  • the M-containing intermediate product is mainly nano-oxidized M
  • the Ti-containing intermediate product is mainly nano titanate
  • the nano-titanate in the composite nano-metal oxide intermediate product containing M and Ti is converted into nano-titanium acid, that is, nano-titanium
  • the acid salt undergoes replacement of H + with titanate cations.
  • the shape of the nano-titanate includes at least one of film, tube, rod, and fiber; wherein, the higher the C 2 concentration, the easier it is for the nano-titanate to form a tube, rod, or fiber;
  • the Ti-containing intermediate product is mainly nano titanic acid
  • composition of the composite nano-metal oxide intermediate product containing M and Ti includes nano-oxide M and at least one of nano-titanate and nano-titanic acid;
  • the shape of the nano titanate includes at least one of film, tube, rod, and fiber; and the film thickness is 0.5nm-10nm; the cross-sectional diameter of the tube, rod, and fiber is 2nm-20nm. ;
  • the shape of the nano titanic acid includes at least one of film, tube, rod, and fiber; and the film thickness is 0.5nm-10nm; the cross-sectional diameter of the tube, rod, and fiber is 2nm-20nm;
  • the method of compounding the M-containing intermediate product and the Ti-containing intermediate product includes in-situ embedded compounding; the characteristics and explanation of the in-situ embedded compounding have been described on the one hand, see the first aspect; here and the first aspect thereof The only difference is: on the one hand, the Ti-containing intermediate product is mainly in the form of a film, while the shape of the Ti-containing intermediate product here includes at least one of film, tube, rod, and fiber;
  • the method of composite of the nano-oxide M and nano-titanate includes in-situ embedded composite
  • the method of composite of the nano-oxidized M and nano-titanic acid includes in-situ embedded composite
  • the nano-oxide M includes at least one of low crystallinity nano-oxide M, crystalline nano-oxide M, and hydrated nano-oxide M;
  • the low crystallinity nano-oxide M includes amorphous nano-oxide M
  • nanometer hydroxide M can be regarded as a combination of nanometer oxide M and H 2 O, nanometer oxide M can be obtained by heating and dehydration at a lower temperature, so the hydrated nanometer oxide M is nanometer hydroxide M;
  • nano-oxide M has particle dispersibility
  • oxidized Mn can be MnO or MnO 2 ;
  • the shape of the nano-oxide M has at least one dimension in the three-dimensional direction not exceeding 500 nm;
  • the shape of the nano-oxide M has at least one dimension in the three-dimensional direction not exceeding 250 nm;
  • the shape of the nano-oxide M has at least one dimension in the three-dimensional direction not exceeding 150 nm;
  • the shape of the nano-oxide M includes at least one of film, granular, plate, strip, tube-rod, and floc; the floc refers to extremely small and without obvious edges and corners. The state in which microstructures are clustered together.
  • nano-oxide M can be softly agglomerated together, they are not closely connected through a three-dimensional continuous rigid network structure and maintain the shape of the original initial alloy.
  • the nano-oxide M is mainly in the form of a film, its thickness is 0.25nm to 30nm; and the average area of the film is greater than 100nm 2 ;
  • the nano-oxide M is mainly in the form of particles, its particle size range is 1.5nm ⁇ 500nm; preferably 1.5nm ⁇ 200nm; preferably 1.5nm ⁇ 100nm;
  • the nano-oxide M when the nano-oxide M is mainly in the form of plates, its thickness ranges from 1.5nm to 100nm, preferably from 5nm to 30nm, and further preferably from 5nm to 20nm; and the average area of the plates is greater than 100nm 2 ;
  • the size of its flocculation microstructure is 1 nm to 15 nm;
  • the nano-oxide M when it is mainly in the shape of a tube or rod, it includes a tube shape or a rod shape, and its diameter ranges from 2 nm to 200 nm; further preferably, it is from 2 nm to 50 nm; and its aspect ratio is greater than 2;
  • the morphological characteristics of the nano-oxide M, nano-titanate, nano-hydroxide D or DO 2 involved are the characteristics displayed when the corresponding component volume dominates. ; When a certain intermediate component does not dominate in volume, it may not show the morphological characteristics when its volume dominates due to the interaction between various intermediate components.
  • the intermediate component of nano-titanate can appear in a tubular state when it is compounded with nano-oxidized Nb and its volume percentage exceeds 50%. However, when its volume percentage is less than 20%, it is affected by nano-oxidation. Due to the influence of Nb (if it is embedded in it), it may not show a tubular state.
  • thermal stability or (and) crystallization temperature of the composite nanometer metal oxide intermediate product is higher than the thermal stability or (and) crystallization temperature of the corresponding single nanometer metal oxide intermediate product prepared by a similar process.
  • This increase in thermal stability or/or crystallization temperature is related to the special combination of different A-type sub-elements (element Ti, M-type sub-elements, D-type sub-elements) in the composite nano-metal oxide intermediate.
  • This kind of composite that improves thermal stability or (and) crystallization temperature includes two types: one is the initial in-situ embedded composite, including in-situ embedded composites of atoms, atomic clusters, and phase scales; the other is ultra-fine, Physical adsorption composite involving ultra-highly dispersed flocculent hydrogen oxide D will induce sintering embedded composite during the later heat treatment process.
  • the composite nanometer metal oxide intermediate product contains at least two of the three types of sub-elements: element Ti, M-type sub-elements, and D-type sub-elements; and the composite nanometer metal oxide intermediate product, At least two of the three types of sub-elements, Ti element, M-type sub-element, and D-type sub-element, are at the atomic/atom cluster scale or fine phase (abbreviation for fine phase) scale where heterogeneous elements correspond to oxide intermediates.
  • the composite wherein the atom/atom cluster scale size is 0.25nm-2.5nm; the average particle size of the fine phase is less than 250nm;
  • At least two types of sub-elements among the three types of sub-elements: Ti element, M-type sub-elements, and D-type sub-elements are processed at the atomic/atom cluster scale or the fine phase scale.
  • the temperature of the heat treatment is 300°C to 2000°C; further, the temperature of the heat treatment is 400°C to 2000°C; further, the temperature of the heat treatment is 500°C to 2000°C;
  • the heat treatment time is 1min ⁇ 24h; further, the heat treatment time is 5min ⁇ 24h;
  • the heat treatment time is 30min ⁇ 24h
  • the three types of elements Ti element, M-type sub-elements, and D-type sub-elements, are present at the atomic/atom cluster scale or fine phase (abbreviation for fine phase).
  • the scale is used to perform the compounding of heterogeneous elements; wherein the scale size of the atom/atom cluster is 0.25nm-2.5nm; the average particle size of the fine phase is less than 250nm;
  • phase corresponding to the Ti element is partially crystallized or fully crystallized nano-TiO 2 ;
  • phase corresponding to the M-type sub-element is partially crystallized or fully crystallized nano-oxide M, the D-type sub-element
  • the phase corresponding to the element is partially crystallized or fully crystallized nano-DO 2 ;
  • the average particle size of the fine phase is lower than 125 nm; further, the average particle size of the fine phase is lower than 50 nm;
  • the average particle size of the fine phase is lower than 25 nm; further, the average particle size of the fine phase is lower than 15 nm;
  • the atom/atom cluster scale is 0.25nm-2.5nm; the atomic scale is 0.25nm-0.5nm, and the atomic cluster scale is 0.5nm-2.5nm; at the 0.25nm-2.5nm scale, it is not enough to form a phase and can only Called atoms or clusters of atoms;
  • the three types of elements, Ti element, M-type sub-elements, and D-type sub-elements are combined with heterogeneous elements at the atomic/atomic cluster scale; wherein, the atoms /The size of the atomic cluster is 0.25nm-2.5nm.
  • the degree of crystallization of the phase corresponding to each sub-category of A-type elements is related to the heat treatment temperature and time; according to the phase transformation law, partially crystallized nano-TiO 2 may contain titanic acid components; partially crystallized nano-TiO 2 Oxidized M may contain a hydroxide component of M; partially crystallized nano-DO 2 may contain a hydroxide component of D.
  • the three types of elements are compounded of heterogeneous elements at the atomic/atomic cluster scale or fine phase scale; wherein , the scale size of the atoms/atom clusters is 0.25nm-2.5nm; the average particle size of the fine phase is less than 250nm
  • the Ti element, M type The corresponding components of sub-elements and D-type sub-elements are judged separately.
  • the particle size of the smaller components is either at the atomic/atom cluster level (0.25nm-2.5nm), or the average particle size is less than 250nm.
  • Fine phase level For example: If the composite nanometal oxide with increased crystallization is (TiCr)O 2 , which is formed by inserting a small amount of Cr into TiO 2 with atoms or atomic clusters, then the Ti element and Cr element (belonging to the M-type sub-elements) are The composite of heterogeneous elements is carried out at the atomic/atom cluster scale; if the composite nanometal oxide with an increased degree of crystallization is the ZrO 2 phase and is composited with the Cr oxide phase, the average particle size of the smaller phase between the two is The fine phase level is lower than 250nm and larger than 2.5nm, that is, the fine phase is expressed as the situation where two or more phases appear, and the fine phase is the phase with the smaller average size.
  • the composite nano-metal oxide with an increased degree of crystallization when the three types of elements, Ti element, M-type sub-elements, and D-type sub-elements, are combined with heterogeneous elements at the fine phase scale, the composite nano-metal oxide
  • the evolution rules and product characteristics during the heat treatment process include the following characteristics:
  • the composite nanometal oxide is mainly a composite of nanometer oxide M and nanometer TiO 2 ; and the method of composite of the nanometer oxide M and nanometer TiO 2 includes in-situ embedded composite ;
  • the composite nanometal oxide is mainly a composite of nanometer DO 2 and nanometer oxide M or (with) nanometer TiO 2 ; and when the composite nanometer metal oxide also includes nanometer
  • the composite method of nano-oxidizing M and nano-TiO 2 includes in-situ embedded composite.
  • the composite of nano-DO 2 and nano-oxide M or (with) nano-TiO 2 includes three situations: the composite of nano-DO 2 and nano-oxide M; the composite of nano-DO 2 and nano-TiO 2 ; nano-DO 2 Composite with nano-oxide M and nano-TiO 2 ;
  • the nano-titanic acid in the composite nano-metal oxide intermediate product gradually transforms into anatase TiO 2 and then further into rutile type TiO 2 transformation;
  • the nano-hydroxide D in the composite nano-metal oxide intermediate product gradually transforms into crystalline nano-DO 2; wherein, the crystalline nano-DO 2 State DO 2 includes at least one of three situations: ZrO 2 , HfO 2 , (Zr/Hf)O 2 ;
  • the degree of transformation of the composite nanometal oxide intermediate product in the above three cases a)-c) is related to the heat treatment time and temperature. Under certain heat treatment time and temperature conditions, products with any degree of crystallization (crystallinity 0-100%) are within the scope of protection of this application; as long as the heat treatment time is long enough and the temperature is high enough, the composite nano-metal oxide intermediate product The above-mentioned transformations a)-c) can all occur completely.
  • the composite nano-metal oxide intermediate product is originally in an in-situ embedded state, such as the in-situ embedded composite of nano-M oxide and nano-titanic acid, which is in the best and uniformly dispersed state before sintering, it can still be produced after sintering. Obtain the best uniform dispersion state;
  • the particle porosity or (and) specific surface area of the composite nanometal oxide is higher than the particle porosity or (and) specific surface area of the corresponding single nanometal oxide prepared by a similar process.
  • the reasons for this phenomenon are similar to the reasons for the thermal stability of the composite nanometal oxide intermediate product or (and) the increase in crystallization temperature, and are related to the initial in-situ embedded composite or the sintering embedded composite induced by heat treatment.
  • the particle porosity or (and) specific surface area of a composite nanometal oxide composed of Zr and Ti elements is higher than that of a nanometal oxide composed of Zr alone or Ti element alone. ) specific surface area.
  • the particle porosity or specific surface area of the composite nano-metal oxide with an increased degree of crystallization is increased, it is easier to obtain finer particles of the composite nano-metal oxide with an increased degree of crystallization through subsequent sand grinding and ball milling.
  • phase composition of the flake crystalline nano-TiO 2 in the composite nano-metal oxide includes at least one of brookite-type TiO 2 , nano-anatase nano-TiO 2 , and rutile-type nano-TiO 2 ; Diameter is 3nm ⁇ 500nm;
  • the particle size of the crystalline nano-DO 2 is 3 nm to 500 nm;
  • the nano-oxidized M has a tendency to evolve into crystalline nano-oxidized M after heat treatment; its shape includes at least one of film, granular, plate, strip, tube and rod, and sintered agglomerate;
  • oxidized Mn can be MnO or MnO 2 ;
  • the shape of the crystalline nanooxide M is a film
  • its thickness is 2 nm to 20 nm; more preferably, it is 3 nm to 10 nm; the average area of the film is greater than 200 nm 2 ;
  • the shape of the crystalline nanooxide M is granular, its particle size ranges from 3 nm to 500 nm;
  • the shape of the crystalline nanooxide M is plate-like, its thickness is 6 nm to 75 nm, and the average area of the plate is greater than 30 nm 2 ;
  • the shape of the crystalline nanooxide M is a strip, its diameter ranges from 3 nm to 60 nm, and the aspect ratio is greater than 4;
  • the shape of the crystalline nanooxide M is a tube-rod shape, it includes a tube shape and a rod shape, its diameter ranges from 3 nm to 200 nm, and its aspect ratio is greater than 2;
  • the shape of the crystalline nano-oxide M is sintered agglomeration, its particle size is significantly increased due to sintering agglomeration, and the particle size range is 5 nm to 1 mm.
  • the composite nano-metal oxide with an increased degree of crystallization contains at least two of the three sub-elements: Ti, M-type sub-elements, and D-type sub-elements; and the composite nano-metal oxide has , at least two types of sub-elements among the three types of sub-elements: Ti element, M-type sub-elements, and D-type sub-elements, perform the corresponding oxides of heterogeneous elements at the scale of atoms/atom clusters or fine phases (abbreviation for fine phases).
  • Composite wherein the atom/atom cluster size is 0.25nm-2.5nm; the average particle size of the fine phase is less than 250nm;
  • At least two types of sub-elements among the three types of sub-elements: Ti element, M-type sub-elements, and D-type sub-elements are dissimilar elements at the atomic/atom cluster scale or the fine phase scale.
  • In-situ embedded composite of corresponding oxides are dissimilar elements at the atomic/atom cluster scale or the fine phase scale.
  • Its fourth aspect is a preparation method of composite nanometer metal oxide intermediate product, which is characterized by including the following steps:
  • Step 1) the process is completely consistent with the process described in the three aspects of step (1), see the three aspects for details;
  • Step 2 the process is completely consistent with the process described in the three aspects of step (2), see the three aspects for details;
  • Step 3 the process is completely consistent with the process described in the three aspects of step (3), see the three aspects for details;
  • Step 4 the process is completely consistent with the process described in the three aspects of step (4), see the three aspects for details;
  • step 4
  • the Ti-containing intermediate product when the Ti-containing intermediate product is in phase, its shape includes at least one of film, tube, rod, and fiber.
  • the Ti-containing intermediate product when the Ti-containing intermediate product is in phase, its shape includes at least one of tubular, rod-like, and fibrous shapes.
  • steps 1) to steps 4) are completely consistent with its three aspects of steps (1) to steps (4), including detailed descriptions of each sub-step. For details, please refer to its three aspects of steps (1) to steps (4). ) and will not be repeated here.
  • the present application also relates to a composite nanometal oxide, which is characterized in that it is prepared according to the preparation method described in one aspect.
  • the preparation process and detailed features are described in steps one to four in one aspect.
  • the detailed features also includes:
  • the composite nanometal oxide contains at least two of the three subelements: Ti, M subelements, and D subelements; and the composite nanometal oxide contains Ti elements, M subelements, and D subelements.
  • D-type sub-elements at least two types of sub-elements among these three types of sub-elements perform the compounding of corresponding oxides of heterogeneous elements at the scale of atoms/atom clusters or fine phases (abbreviation for fine phases); wherein, the atoms/ The size of the atomic cluster is 0.25nm-2.5nm; the average particle size of the fine phase is less than 250nm; among them, the M-type sub-elements include Cr, V, Nb, Ta, W, Mo, Mn, Y, La, Ce, At least one of Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu; type D sub-elements include at least one of Zr
  • At least two types of sub-elements among the three types of sub-elements: Ti element, M-type sub-elements, and D-type sub-elements are dissimilar elements at the atomic/atom cluster scale or the fine phase scale.
  • In-situ embedded composite of corresponding oxides are dissimilar elements at the atomic/atom cluster scale or the fine phase scale.
  • the present application also relates to a composite nanometal oxide intermediate product, which is characterized in that it is prepared according to the preparation method described in the second aspect.
  • the preparation process and detailed characteristics are as described in steps one to three of the second aspect, and Detailed features also include:
  • the composite nanometer metal oxide intermediate product contains at least two of the three types of sub-elements: element Ti, M-type sub-elements, and D-type sub-elements; and in the composite nano-metal oxide intermediate product, the Ti element, At least two of the three types of sub-elements, M-type sub-elements and D-type sub-elements, perform the compounding of corresponding oxide intermediates of heterogeneous elements at the atomic/atom cluster scale or the fine phase (abbreviation for fine phase) scale; Wherein, the size of the atom/atom cluster is 0.25nm-2.5nm; the average particle size of the fine phase is less than 250nm;
  • At least two types of sub-elements among the three types of sub-elements: Ti element, M-type sub-elements, and D-type sub-elements are processed at the atomic/atom cluster scale or the fine phase scale.
  • the present application also relates to a composite nanometal oxide, which is characterized in that it is prepared according to the preparation method described in the third aspect, and its preparation process and detailed characteristics are as described in the third aspect.
  • this application also relates to a composite nanometal oxide intermediate product, which is characterized in that it is prepared according to the preparation method described in the fourth aspect, and its preparation process and detailed characteristics are as described in the fourth aspect.
  • this application also relates to product materials prepared by the preparation method described in any one of its first to fourth aspects, or to materials described in its fifth to eighth aspects, in composite materials, catalytic materials, ceramic materials, refractory materials, Applications in advanced electronic materials, battery materials, color-changing materials, absorbing materials, sewage degradation materials, sterilization materials, coatings, pigments, thermal spray materials, and sensors.
  • a method for preparing composite oxide ceramics is characterized by including the following steps:
  • Step S1 prepare a uniformly mixed and refined mixed powder.
  • the composition of the mixed powder includes the composite nanometal oxide or intermediate product prepared by the preparation method according to any one of the first aspect to the fourth aspect, and additional powder. body; wherein, the molar percentage content of the composite nanometal oxide or intermediate product in the mixed powder is V 1 , the molar percentage content of the additional powder in the mixed powder is V 2 , and the additional powder includes At least one of Al 2 O 3 , CaO, MgO, SiO 2 , B 2 O 3 and BeO, 1% ⁇ V 1 ⁇ 100%, 0 ⁇ V 2 ⁇ 99%;
  • step S2 the mixed powder is pressed into a green body and roasted at high temperature to obtain a composite oxide ceramic material.
  • the mixed powder contains, in addition to the composite nanometal oxide or intermediate product prepared by the preparation method described in any one of the first to the fourth aspects, additional powder components, so it needs to be mixed During the feeding process, the mixed powder is evenly mixed and refined at the same time;
  • the process of preparing uniformly mixed and refined mixed powder includes at least one of ball milling and sand milling; when the mixing process is a wet method, after the mixing process is completed, the uniformly mixed and refined powder is obtained by drying. Refined mixed powder; during the mixing process, the powder is broken and refined at the same time;
  • the composite nanometal oxide or intermediate product prepared by the preparation method according to any one of the first aspect to the fourth aspect contains D hydroxide or (with) DO 2 ;
  • the composite nanometal oxide or intermediate product prepared by the preparation method of any one of the first aspect to the fourth aspect thereof contains DO 2 and oxidized Y;
  • the molar percentage content of ZrO 2 in the composite nanometal oxide or intermediate product prepared by the preparation method described in any one of the first aspect to the fourth aspect is greater than 50%;
  • the molar percentage of ZrO 2 in the mixed powder is greater than 25%; further, the molar percentage of ZrO 2 in the mixed powder is greater than 50%; further, the ZrO in the mixed powder The molar percentage of 2 is greater than 75%;
  • the molar percentage of ZrO 2 in the mixed powder is greater than 75%, and the mixed powder includes composite nano-metal oxides composed of ZrO 2 and Y 2 O 3 ;
  • the molding pressure of the pressed green body is 5MPa ⁇ 800MPa; further, the molding pressure of the pressed green body is 5MPa ⁇ 80MPa;
  • the calcination temperature is 500°C to 2000°C; further, the calcination temperature is 500°C to 1500°C;
  • the pressing to form a green body includes at least one of two schemes: pressing while heating and roasting, or pressing first and then roasting.
  • a composite oxide ceramic is characterized in that it is prepared according to the preparation method described in its tenth aspect, and its detailed features are as described in its tenth aspect.
  • composite nanometal oxides with multiple components can be prepared at one time.
  • the traditional method first requires the preparation of three nanometal oxides of Nb 2 O 5 , TiO 2 and ZrO 2 respectively. Then mix them evenly to obtain composite nanometer metal oxide. Due to the agglomeration problem of powder materials, it is difficult to ensure uniform mixing, and all mixing is physical mixing.
  • a further improved method can be to separately prepare the Nb-T intermetallic compound initial alloy, the Ti-T intermetallic compound initial alloy, and the Zr-T intermetallic compound initial alloy, and then mix the three intermetallic compound alloys and then proceed with the present application. Similar hydrogen evolution and deT reaction process. Although this method has been improved, there are two disadvantages: it is necessary to prepare an initial alloy of three intermetallic compounds; since Nb and Ti belong to different intermetallic compounds in the initial alloy, it is difficult to ensure the in-situ embedded composite. Nb-containing intermediate products and Ti-containing intermediate products.
  • the molar ratio of Nb, Ti, and Zr in the composite nanometal oxide can be designed through an initial alloy.
  • the large solid solubility of each element in the Al-(Nb/Ti/Zr) intermetallic compound for example, in the TiAl 3 intermetallic compound, the original 25% Ti, if 5% of the Ti
  • the obtained Ti(Nb)Al 3 intermetallic compound still has almost the same crystal structure as the TiAl 3 intermetallic compound.
  • Nb and Ti exist in an intermetallic compound at the same time.
  • the evolution processes of the two are carried out in situ at the same time.
  • the reaction requires the use of a high-pressure reaction vessel, which generally uses nano-TiO 2 and high-concentration strong alkali (such as NaOH solution) as raw material, hydrothermal synthesis is carried out under high temperature conditions for a very long time, and titanate (such as sodium titanate) is obtained through the reaction. After neutralization and pickling, titanate nanotubes are generally obtained.
  • a high-pressure reaction vessel which generally uses nano-TiO 2 and high-concentration strong alkali (such as NaOH solution) as raw material
  • hydrothermal synthesis is carried out under high temperature conditions for a very long time, and titanate (such as sodium titanate) is obtained through the reaction. After neutralization and pickling, titanate nanotubes are generally obtained.
  • titanate nanotubes with an inner diameter of 5.3nm.
  • Other preparation methods also include: weighing NaOH and commercial TiO 2 according to the measurement relationship and moving them into a polytetrafluoroethylene high-pressure reactor. After mixing, keep the mixture at 230°C for 48h to 96h. After cooling to room temperature, take it out, wash and dry. Finally, sodium titanate nanotubes are obtained, and further pickled to obtain titanate nanotubes.
  • the characteristics of the traditional strong alkali hydrothermal method are: 1) using TiO 2 as the titanium source; 2) being carried out in a high-pressure reaction vessel, requiring closed high-pressure conditions; 3) being carried out at a higher temperature; 4) requiring a lot of A long reaction time can first destroy the stable O-Ti bond and then re-form the O-Ti bond, and the reaction time is calculated in tens of hours; 5)
  • the obtained product is generally titanate nanotubes or titanate nanotubes.
  • this application also uses a strong alkali solution when preparing nanocomposite metal oxides containing nanotitanates, but it is significantly different from the traditional strong alkali hydrothermal method: 1) using Ti-containing intermetallic
  • the compound is a titanium source; 2) the reaction can be carried out in an open vessel and under normal pressure, and does not necessarily require a high-pressure sealed vessel; 3) it is preferably carried out near the boiling point of the alkali solution, and the upper limit of the temperature is the boiling point of the alkali solution, which is very easy to accurately Control; 4)
  • the reaction can be completed within minutes or even tens of seconds. Therefore, this application cleverly changes the traditional oxide raw materials into the initial alloy raw materials of intermetallic compounds, which greatly shortens the time required for the reaction and improves the efficiency.
  • This obvious beneficial effect is closely related to the reaction of the initial alloy at a higher temperature, especially preferably the boiling point temperature T f solution of the alkali solution.
  • the solution composition of the reaction system has obvious particularities, as shown in the following: far below the boiling point of the solution, the solvent mainly exists as liquid water; but at the boiling point of the solution or When the temperature is very close to the boiling point, in addition to liquid water and a large amount of highly active gaseous water (gaseous water produced by evaporation at the boiling point temperature), the solvent also contains highly active water that is transforming from liquid water to gaseous water.
  • the content and state of atmospheric ambient gases (oxygen, nitrogen) dissolved in the solvent are also extremely special (because the large amounts of water vapor and hydrogen appear, changing the saturation partial pressure conditions of dissolved gases in water).
  • the large amount of hydrogen generated by the reaction between AT intermetallic compounds and concentrated alkali solutions, as well as the small amount of salt dissolved in the solution will change the material composition of the reaction system, which provides a very special reaction environment for the reaction.
  • This special reaction environment can greatly shorten the preparation time of the target product.
  • the traditional high-pressure hydrothermal method to prepare nano-titanate films uses extremely stable TiO 2 as the Ti source, and requires a high-pressure, high-temperature, and long-term reaction to first destroy the Ti-O bond structure of TiO 2 , only after the Ti-O bond is destroyed, new intermediate products and final products can be further generated, and the time required is generally calculated in hours.
  • the concentration of alkali in the solution is determined, the boiling point temperature to which the solution can be heated under normal pressure is also determined, which means that the pressure and temperature in the reaction conditions are accurately determined. At the boiling point T f of the solution, any additional excess heat in the solution will be converted into the heat of vaporization of water without increasing the temperature of the solution.
  • the present application found that when the AT intermetallic compound reacts with an alkali solution of a certain temperature and concentration, and the reaction rate exceeds 2 ⁇ m/min, especially preferably the boiling point temperature of the alkali solution, the initial alloy can be quickly and completely destroyed.
  • the shape realizes the nano-fragmentation of the original alloy, and at the same time, the shape and composition are reconstructed to generate nano-scale solid matter containing M or (and) Ti with particle dispersion.
  • the product prepared by de-alloying at room temperature or lower temperature is generally nano-porous metal oxide or nano-porous metal, which still maintains the shape of the original initial alloy particles before the reaction, including its angular shape.
  • this nanoporous structure forms an appearance consistent with the shape of the original initial alloy powder through three-dimensional continuous network connection, and its particle size is still equivalent to the size of the original alloy powder, mainly in the order of several microns or tens of microns.
  • the average particle size of the initial alloy powder is 10 ⁇ m
  • the alkali concentration and alkali temperature after nanodisintegration occurs at a reaction rate exceeding 2 ⁇ m/min, the resulting product has an average particle size of no more than 500 nm.
  • Solid substances containing M or (and) Ti that have particle dispersibility do not contain nanoporous secondary structures inside the particles, and these solid substances containing M or (and) Ti can also be dispersed, although they can be softly agglomerated together, but they are not tightly and rigidly connected through a three-dimensional continuous network structure to maintain the shape of the original initial alloy, including the angular shape of its particles. That is to say, through the preparation method of the present application, regardless of the shape and size of the initial alloy, dispersible nanoscale solid materials containing M or/and Ti can be obtained through nano-fragmentation during the hydrogen evolution and deT reaction.
  • the particle size of the initial alloy is generally larger, such as strips generally thicker than 10 ⁇ m, and the average particle size of powder particles is generally larger than 5 ⁇ m
  • the reaction between AT intermetallic compounds and alkaline solutions at lower temperatures or room temperature generally still results in micron-scale
  • Large-particle nanoporous metal oxides or nanoporous metals are not suitable for many occasions where fine particles and dispersion are required; however, this application has achieved high dispersion of nano-scale M-containing or (with) Ti
  • the preparation of solid-state substances has obvious positive significance.
  • shape reconstruction occurs simultaneously with nanofragmentation.
  • the shape reconstruction refers to the nanoscale product obtained by the hydrogen evolution deT reaction. It is not a simple fragmentation of the nanoporous structure (ligament), but a complete reconstruction. If the low-temperature hydrogen evolution and deT reaction results in a nanoporous structure, and the product obtained by the high temperature hydrogen deT reaction simply fragments the nanoporous structure, then it can only be called simple fragmentation, and the product morphology is fragmentation. porous ligament. However, what occurs in the solution described in this application is not this simple fragmentation, but also includes shape reconstruction; various morphologies of solid materials containing M or (with) Ti, such as lath-like structures, flocs, etc.
  • the in-situ embedded composite of M-containing intermediates and Ti-containing intermediates is realized, and even includes the in-situ embedded composite of a small number of D-containing intermediates and M-containing intermediates and/or Ti-containing intermediates.
  • This kind of intercalation is different from the ordinary adsorption combination reported in other literatures that is dominated by van der Waals force physical adsorption (nanoparticles adsorbed by van der Waals force can move and fall off). It can ensure M-containing intermediate products, Ti-containing intermediate products, and D-containing intermediates. The products can be closely embedded with each other (cannot move or fall off), thereby obtaining more excellent properties.
  • this application found that when the D-type elements (Zr, Hf elements) in the initial alloy react with a hot concentrated alkali solution, the Zr and Hf elements can be dissolved in the hot concentrated alkali solution, and this The solubility increases significantly with increasing temperature. This dissolution phenomenon is most pronounced when the reaction takes place under normal pressure and preferably at the boiling point of the alkali solution.
  • the dissolution here does not mean dissolution in a narrow sense, but specifically refers to the intermetallic compound containing D elements being dissolved in an excess of hot concentrated alkali solution in a complex-like manner or in other unknown ways after a series of reactions. middle.
  • the solubility characteristics of Zr and Hf elements are related to the concentration of the alkali solution.
  • crystalline nano- ZrO has been a key raw material for advanced ceramic materials.
  • the preparation method of low-cost crystalline nano-ZrO 2 mainly involves first preparing zirconium hydroxide precursor (such as the reaction of zirconium oxychloride and ammonia water to precipitate zirconium hydroxide flocculent precipitate), then heat treatment and sintering to obtain crystalline ZrO 2 , and finally The crystalline ZrO 2 obtained by sintering is dispersed and refined through ball milling or sand grinding to obtain crystalline nano-ZrO 2 powder particles, an important raw material for advanced ceramic products, and the finer the powder particles, the better the performance.
  • this application first prepares composite nanometal and oxide intermediates of zirconium hydroxide and Ti-containing intermediates or (with) M-containing intermediates, so that in the subsequent high-temperature sintering process , the obtained Ti-containing intermediate product or (and) M-containing intermediate product doped composite crystalline ZrO 2 has good microscopic looseness and dispersion characteristics, which can be well dispersed and refined through subsequent ball milling or sanding.
  • dispersed crystalline ZrO 2 composed of single or very few crystal grains and compounded by doping is prepared (see Figures 7-8 of Example 1).
  • This technology not only solves the dispersion and particle size problems of sintered crystalline ZrO 2 , but also allows the components participating in the composite to be fully and uniformly mixed with crystalline ZrO 2 through in-situ compounding.
  • the composite component includes Cr 2 O 3 (a raw material for high-end refractory materials and often used as a high-end green inorganic pigment)
  • it can not only significantly increase the heat-resistant temperature of ZrO 2 -Cr 2 O 3 ceramic products, but also obtain Coloring effects.
  • composite nanometal oxide intermediates with increased thermal stability or/and crystallization temperature can be prepared, as well as composite nanometal oxides with increased particle porosity or specific surface area.
  • the composite nanometal oxide or intermediate product prepared by the preparation method described in any one of the first to fourth aspects of this application has been fully mixed during the preparation process, especially the in-situ embedded corresponding mixing, which is extremely The cost required for uniform mixing between the components of the composite nanometal oxide is greatly reduced.
  • the reaction time ranges from tens of seconds to several minutes; the reaction conditions can be precisely controlled and the reaction can be terminated quickly.
  • the technical solution and preparation method involved in the present invention have the characteristics of simple process, easy control, high efficiency, and low cost. It can prepare a variety of composite nano-metal oxides and is suitable for use in composite materials, catalytic materials, ceramic materials, and refractory materials. Materials, advanced electronic materials, battery materials, color-changing materials, absorbing materials, sewage degradation materials, sterilization materials, coatings, pigments, thermal spray materials, and sensors.
  • Figure 1 is a low-magnification SEM photo of the initial alloy solidification structure of Example 1;
  • Figure 2 is a high-magnification SEM photo of the initial alloy solidification structure of Example 1;
  • Figure 3 is a low-magnification TEM photo and diffraction spectrum of the composite nanometal oxide intermediate prepared in Example 1;
  • Figure 4 is a medium-magnification and high-magnification TEM photograph of the composite nano-metal oxide intermediate prepared in Example 1;
  • Figure 5 is a low-magnification TEM photograph and diffraction spectrum of the composite nanometal oxide prepared in Example 1 after heat treatment at 600°C;
  • Figure 6 is a medium-magnification and high-magnification TEM photograph of the composite nanometal oxide prepared in Example 1 after heat treatment at 600°C;
  • Figure 7 is a low-magnification TEM photograph and diffraction spectrum of the composite nanometal oxide prepared in Example 1 after heat treatment at 900°C;
  • Figure 8 is a medium-magnification and high-magnification TEM photograph of the composite nanometal oxide prepared in Example 1 after heat treatment at 900°C;
  • Figure 9 is an SEM photo of the initial alloy solidification structure of Example 2.
  • Figure 10 is the XRD spectrum of the composite nanometal oxide intermediate product prepared in Example 2, the composite nanometal oxide heat treated at 650°C, and the heat treated at 900°C;
  • Figure 11 is a low-magnification TEM photo and diffraction spectrum of the composite nanometal oxide intermediate prepared in Example 3;
  • Figure 12 is a high-magnification TEM photo of the composite nanometal oxide intermediate prepared in Example 3.
  • Figure 13 is a low-magnification TEM photo of the composite nanometal oxide prepared in Example 3 after heat treatment at 900°C;
  • Figure 14 is a medium-magnification and high-magnification TEM photograph of the composite nanometal oxide prepared in Example 3 after heat treatment at 900°C;
  • Figure 15 is a low-magnification TEM photo and diffraction spectrum of the composite nanometal oxide intermediate prepared in Example 4.
  • Figure 16 is a high-magnification TEM photo of the composite nanometal oxide intermediate prepared in Example 4.
  • Figure 17 is a low-magnification TEM photo and diffraction spectrum of the composite nanometal oxide intermediate prepared in Example 5;
  • Figure 18 is a medium-magnification and high-magnification TEM photograph of the composite nanometal oxide prepared in Example 5 after heat treatment at 1100°C;
  • Figure 19 is a low-magnification TEM photo and diffraction spectrum of the composite nanometal oxide intermediate prepared in Example 6;
  • Figure 20 is a low-magnification and high-magnification SEM photo of the product obtained in Comparative Example 1;
  • Figure 21 is a low-magnification TEM photo and diffraction spectrum of the low crystallinity Zr hydroxide nanoparticles prepared in Comparative Example 2;
  • Figure 22 is a high-magnification TEM photo of the low crystallinity nano-Zr hydroxide prepared in Comparative Example 2;
  • Figure 23 is a low-magnification TEM photograph and diffraction spectrum of nano-Zr oxide after heat treatment at 600°C prepared in Comparative Example 2;
  • Figure 24 is a high-magnification TEM photograph of nano-Zr oxide after heat treatment at 600°C prepared in Comparative Example 2;
  • Figure 25 is a low-magnification TEM photograph and diffraction spectrum of nano-Zr oxide after heat treatment at 900°C prepared in Comparative Example 2;
  • Figure 26 is a high-magnification TEM photograph of nano-Zr oxide prepared in Comparative Example 2 after heat treatment at 900°C.
  • This embodiment provides a method for preparing composite nanometal oxides and composite oxide ceramics containing Zr, Nb and Ti elements, including the following steps:
  • the alloy melt solidifies into alloy ingots and is broken into initial alloy powder with an average particle size of 100 ⁇ m.
  • the solidification structure phase composition is mainly composed of approximately Al 73 Zr 20 Ti 3 Nb 4 and Al 76 Zr 13 Ti 10 Nb 1 . It is composed of two intermetallic compounds, and is mainly composed of intermetallic compounds of about Al 73 Zr 20 Ti 3 Nb 4.
  • the intermetallic compound of Al 73 Zr 20 Ti 3 Nb 4 may be the Al 3 Zr phase with Ti and Nb in solid solution;
  • the intermetallic compound of Al 76 Zr 13 Ti 10 Nb 1 may be Al 3 with Nb in solid solution ( Zr-Ti) phase;
  • the size of a single microstructure is much smaller than 20nm;
  • the composite nanometer metal oxide intermediate product ( its low-magnification, medium-magnification and high-magnification TEM morphology and diffraction spectrum are shown in Figure 3-4; it can be seen from Figure 3 that the average particle size of the composite nanometer metal oxide intermediate agglomerate is low At 250nm, as can be seen from the high-magnification photo illustration in Figure 4, the composite nanometal oxide intermediate product agglomerates are composed of finer flocculent microstructures, which are mainly composed of colloidal flocculent Zr hydroxide. Since the agglomerates are amorphous, , so it is difficult to observe the details of the microstructure.
  • the pure Al-Nb intermetallic compound obtained under the above reaction conditions is also colloidal flocculent hydroxide Nb or amorphous oxidized Nb, it cannot be compared with colloidal flocculent Zr hydroxide through TEM contrast from Figure 3-4. Distinguish between them; since Ti accounts for less of the total molar percentage of Zr, Ti, and Nb in the initial alloy, and the molar percentages of Nb and Ti are almost the same, the Ti-containing intermediate product and the Nb-containing intermediate product are in the hydrogen evolution and deAl reaction.
  • the Ti-containing intermediate product When generated simultaneously during the process, the Ti-containing intermediate product failed to form as a two-dimensional nano-titanate film (the pure Al-Ti intermetallic compound obtained two-dimensional nano-titanate with a thickness of 0.5nm-4nm under the above reaction conditions Nano film, after pickling, it becomes a two-dimensional nano titanate film with a thickness of 0.5nm-4nm); based on this, it can be judged that the Ti-containing intermediate product and the Nb-containing intermediate product have fully recombinated while being generated, which may be Some kind of colloidal flocculent intermediate product containing Ti/Nb exists, and it is difficult to distinguish the contrast from colloidal Zr hydroxide. Among them, Ti-containing intermediates, Nb-containing intermediates, and a small amount of Zr-containing intermediates generated at the same time undergo in-situ embedded composite at the scale of atoms or atomic clusters.
  • This structure makes the prepared composite nanometal oxide have high particle porosity. or specific surface area.
  • the pure Al 3 Zr intermetallic compound reacted under similar conditions according to this example to first obtain colloidal nano-hydroxide Zr (as shown in Figures 21-22); when the pure colloidal flocculated After heat treatment of nano-Zr hydroxide at 900°C for 2 hours, crystallized nano-Zr hydroxide is obtained, as shown in Figure 25-26.
  • they are polycrystalline particles, they are sintered and agglomerated into solid large particles, completely losing the looseness of the particles and showing a low specific surface area.
  • the crystalline composite nanometal oxide containing Ti and Nb elements, mainly nanozirconia, obtained in this example has high particle porosity or specific surface area, which solves the problem of simple nano-oxide obtained by sintering. Zirconium is difficult to further crush and refine, which is an industrial problem.
  • the components of the composite nanometal oxide intermediate product before heat treatment are composed of Ti-containing intermediate products, Nb-containing intermediate products, a small amount of Zr-containing intermediate products, and nano-hydroxide Zr intermediate products that precipitate later. In-situ embedded composites related to chemical interactions were carried out, and this in-situ embedded composite characteristics were retained in the product after heat treatment at 900°C for 2 hours.
  • the above-mentioned crystalline composite nano-metal oxide containing Ti and Nb elements mainly composed of nano-zirconia is broken into crystalline composite nano-metal oxide powder with a particle size of 20nm-40nm (the particle size is is the diameter range of the composite nanometal oxide strip structure before breaking).
  • the obtained crystalline composite nano-metal oxide powder is mixed and pressed into a green body under a pressure of 50MPa. After roasting at 1400°C for 2 hours, a molar ratio Zr:Ti:Nb of about 18:4:3 is obtained, mainly zirconium oxide. of composite nanooxide ceramics.
  • This embodiment provides a method for preparing composite nanometal oxides and composite oxide ceramics containing Zr and Y elements, including the following steps:
  • the mixed colloidal solid material containing Y and Zr is collected, washed with dilute acid, and dried to obtain a composite nanometal oxide intermediate product composed of nanometer yttrium oxide and low crystallinity colloidal Zr hydroxide.
  • the two are uniformly compounded mainly through physical adsorption; among them, the particle size range of nano-yttrium oxide is 3nm ⁇ 200nm; the particle size of the flocculent microstructure of colloidal flocculent Zr hydroxide is 0.5nm-10nm;
  • the composite nano-metal oxide intermediate product does not contain a three-dimensional continuous network-like nano-porous structure or porous skeleton structure; the XRD of the composite nano-metal oxide intermediate product is shown in Figure 10. Due to the low content of yttrium oxide, its XRD peak Only the diffraction information of low crystallinity Zr hydroxide is shown.
  • the above-mentioned composite nano-metal oxide intermediate product containing Y and Zr is heat-treated at 650°C for 1.5 hours to obtain a composite nano-metal oxide uniformly compounded with crystalline nano-yttria and partially crystalline nano-zirconia; among which, crystalline nano-metal oxide is obtained
  • the particle size range of yttrium oxide is 3nm ⁇ 200nm
  • the particle size range of partially crystalline nano-zirconia is 3nm ⁇ 200nm
  • the XRD of the composite nano-metal oxide is shown in Figure 10. Since the nano-Zr oxide is not completely crystallized, The peak intensity is not very obvious, and due to the small content of yttrium oxide, its XRD peak is not obvious.
  • the above-mentioned composite nano-metal oxide after heat treatment at 900°C for 1.5 hours is pressed into a green body under a pressure of 30 MPa, and then roasted at 1450°C for 2 hours to prepare a composite nano-oxide oxide ceramic of yttria-stabilized zirconia, in which the molar ratio Zr:Y is approximately 23.5:1.5.
  • This embodiment provides a method for preparing composite nanometal oxides and composite oxide ceramics containing Hf and Cr elements, including the following steps:
  • the phase composition is mainly composed of Al 3 Hf (Cr) intermetallic compounds containing Cr.
  • Oxide intermediate product its TEM morphology and diffraction spectrum are shown in Figures 11-12; it can be seen from the figure that the average particle size of the composite nanometer metal oxide intermediate product agglomerates is less than 200nm, and the composite nanometer metal oxide intermediate product
  • the agglomerates are composed of finer flocculent microstructures, which are mainly composed of colloidal flocculated Zr hydroxide intermediates, and colloidal flocculated Cr hydroxide or colloidal flocculated Cr oxidation intermediates compounded with them. Since the pure Al-Cr intermetallic compound obtained under the above reaction conditions is also colloidal hydroxide Cr or amorphous oxidized Cr, it cannot be compared with colloidal hydroxide Hf through TEM contrast from Figure 11-12. distinguish; differentiate
  • the above-mentioned composite nano-metal oxide intermediate product is heat-treated at 900°C for 2 hours to obtain a crystalline composite nano-metal oxide composed mainly of nano-oxidized Hf and compounded by oxidized Cr; its low, medium and high magnification TEM morphology As shown in Figure 13-14; it can be seen that the average particle size of the crystalline composite nanometal oxide is less than 50nm, and although a certain degree of sintering agglomeration occurs between these particles, they still maintain a loose sintering agglomeration state. , or a similar nanoporous structure, which is composed of a large number of strip structures with a diameter of 15nm-40nm.
  • This structure makes the prepared composite nanometal oxide have high particle porosity or specific surface area.
  • This loose structure solves the industrial problem that it is difficult to further break and refine the simple nano-oxide Hf obtained by sintering.
  • the existence of this shrinkage structure indicates that before sintering, the uniform composite of the colloidal Zr hydroxide intermediate product and the Cr hydroxide (or Cr oxide) intermediate product occurred on a very small scale.
  • This uniform composite During the sintering process, it evolved into a sintering-induced in-situ embedded composite, thereby changing the morphology and sintering characteristics of the sintered product, and obtaining a crystalline composite nanometal oxide with higher particle porosity or specific surface area. .
  • the above-mentioned crystalline composite nano-metal oxide which is mainly composed of nano-oxide Hf and is compounded by oxidized Cr, is crushed into crystalline composite nano-metal oxide powder with a particle size of 15 nm to 40 nm.
  • the obtained crystalline composite nano-metal oxide powder is mixed and pressed into a green body under a pressure of 50MPa. After roasting at 1250°C for 2 hours, a molar ratio of Hf:Cr is about 5:1, mainly oxidizing Hf and oxidizing Cr. Composite composite nanooxide ceramics.
  • This embodiment provides a composite nanometal oxide containing Ti and Ta elements and a preparation method thereof, which includes the following steps:
  • the phase composition is mainly composed of Al 3 Ti (Ta) intermetallic compounds containing Ta.
  • the intermediate product is a nanometer sodium titanate matrix, which is mainly in the shape of a film, and the film thickness is 0.5nm-5nm, and the average film area is greater than 200nm 2 ;
  • the Ta-containing intermediate product is nanometer oxidized Ta, which is embedded and composited in situ.
  • the mosaic is grown in a nanometer sodium titanate film, and its particle size is 0.5nm-5nm.
  • the composite nano-metal oxide intermediate that participates in the compounding is mainly composed of low-crystallinity nano-titanic acid; its TEM morphology and diffraction spectrum are shown in Figure 15-16; it can be seen from the diffraction pattern that the obtained composite nano-metal oxide intermediate is still It is in a low crystalline state; at this time, the nanometer sodium titanate matrix before pickling has turned into a nanometer titanate matrix, and its shape is still mainly film-like (see Figure 15, especially the ultra-thin film in the lower part of the picture), and the film thickness is 0.5nm-5nm, the average area of the film is greater than 200nm 2 ; the Ta-containing intermediate product is still nano-oxide Ta, which is embedded and grown in
  • the composite nano-metal oxide intermediate product mainly composed of low-crystallinity nano-titanium acid in which the above Ta element participates in the composite is heat-treated at 900°C for 2 hours to obtain a composite nano-metal oxide mainly composed of nano-TiO 2 in which oxidized Ta participates in the composite.
  • the titanate film evolves into plate-like crystalline nano-TiO 2 with a thickness of 2nm-20nm and an average area greater than 100nm 2 ; at the same time, nano-oxide Ta is in-situ embedded and compounded in the plate-like crystalline nano-TiO 2 .
  • This embodiment provides a composite nanometal oxide containing Zr, Hf, Ti and Cr elements and a preparation method thereof, which includes the following steps:
  • Hf and Zr occupy a small molar ratio and are evenly dispersed with Cr and Ti at the atomic scale in intermetallic compounds, when solid flocculent materials containing Cr and Ti are formed, a small part of Hf and Zr are also atomically dispersed. Or embedded in situ in the form of atomic clusters;
  • the Ti intermediate product and a small part of Hf and Zr intermediate products are compounded with oxidized Cr or hydroxide Cr intermediate products through in-situ embedded composite; this in-situ embedded composite includes atoms or atomic clusters
  • the compounding of scales also includes the compounding of fine phase scales.
  • the above-mentioned composite nano-metal oxide intermediate product is heat-treated at 1100°C for 2 hours to obtain a crystalline composite nano-metal oxide in which the oxides of Ti, Hf, and Zr participate in the composite and are mainly composed of nano-Cr oxide; its TEM morphology is as follows As shown in Figure 18; it can be seen from the figure that although the heat treatment temperature is as high as 1100°C, composite nanometal oxides in a loose, sintered and agglomerated state can still be obtained, with particle sizes ranging from 30nm to 150nm; although a certain amount of sintering occurs between the individual particles. agglomeration, but this nanoporous-like structure is easily broken and refined through subsequent ball milling and sanding processes.
  • the above-mentioned Ti, Hf, and Zr oxides participate in the composite and the crystalline composite nanometal oxide mainly composed of nanoscale Cr oxide is broken into crystalline composite nanometal oxide with a particle size of 30nm-150nm. powder.
  • the obtained crystalline composite nano-metal oxide powder is mixed and pressed into a green body under a pressure of 50MPa. After roasting at 1400°C for 2 hours, the molar ratio of Cr:Zr:Hf:Ti is approximately 34:3:1:1. Chromium oxide-based refractory material composed of Ti, Hf, and Zr oxides.
  • This embodiment provides a method for preparing a composite nanometal oxide containing Ti and Mn elements, including the following steps:
  • Ti intermediates and Mn-containing intermediates are formed at the same time, they must have a certain degree of in-situ embedded recombination relationship with each other, including in-situ embedded recombination at the atomic or atomic cluster scale.
  • the composite nanometal oxide intermediate product mainly composed of nanotitanic acid in which Mn participates in the compound is heat-treated at 900°C for 1.5 hours, and the nanotitanic acid film is converted into nanometer TiO 2 sheets, thereby obtaining crystalline nanomanganese oxide and red stone type Composite nano-metal oxide composed of nano-TiO 2 sheets, wherein the thickness of the nano-TiO 2 sheets is 3 nm to 20 nm, and the average area is greater than 150 nm 2 ; the particle size of the crystalline nano-manganese oxide is 3 nm-20 nm; and the crystalline nano-manganese oxide and
  • the main composite method of rutile nano-TiO 2 sheets includes in-situ embedded composite.
  • This embodiment provides a composite nanometal oxide containing Cr and Ti elements and a preparation method thereof, which includes the following steps:
  • an alloy melt mainly composed of Al 61 Cr 35 Ti 4 is obtained by smelting Al, Cr and Ti raw materials, and the alloy melt is quickly solidified through a copper roller.
  • the method is used to prepare an initial alloy strip with a thickness of 20 ⁇ m to 30 ⁇ m and a composition mainly composed of Al 61 Cr 35 Ti 4.
  • Its solidification structure is mainly composed of Al 8 Cr 5 (Ti) intermetallic compounds with Ti dissolved in it.
  • the Al 61 Cr 35 Ti 4 initial alloy strip was reacted with a NaOH aqueous solution, supplemented by 40kHz ultrasonic treatment; where the concentration of the NaOH solution was 15 mol/L, the temperature was 60°C, and the volume of the NaOH solution was Al 61
  • the volume of Cr 35 Ti 4 initial alloy strip is about 100 times; the reaction rate of Al 61 Cr 35 Ti 4 initial alloy strip and NaOH solution is greater than 2 ⁇ m/min.
  • the hydrogen evolution and Al removal reaction is completed, and the initial alloy is removed by hydrogen evolution.
  • the Al reaction undergoes nano-fragmentation, and is simultaneously reconstructed in shape and composition to form a solid colloidal floc intermediate;
  • Composite nano-metal oxide intermediate product composed of oxidized Cr or nano-Cr oxide; its morphology is colloidal floc, and the particle size of the floc microstructure is 0.5nm-10nm. Since the Ti content in the initial alloy is less than the Cr content , Ti-containing intermediate products do not appear in the form of titanate or titanate films, but mainly exist in low-crystalline nano-Cr hydroxide or nano-Cr oxide intermediates through in-situ embedded composite;
  • the composite nano-metal oxide intermediate product mainly composed of low-crystalline nano-Cr hydroxide or nano-Cr oxide in which Ti participates in the composite is heat-treated at 1000°C for 2 hours, and the low-crystalline nano-Cr hydroxide or nano-Cr oxide is converted into crystalline
  • the particle size of the state oxidized Cr particles is 3nm-150nm; at the same time, the Ti-containing components mainly exist in the crystalline oxidized Cr through in-situ embedded composite.
  • This embodiment provides a method for preparing composite nanometal oxides containing Ti and Ta elements, including the following steps:
  • a composite nanometer metal oxide intermediate product composed of a Ta-containing intermediate product and a titanate nanotube intermediate product; it is partially crystalline; wherein the outer diameter of the titanate nanotube intermediate product ranges from 5 nm to 15 nm, and the long diameter is greater than 5; it contains
  • the Ta intermediate product is mainly nano-tantalum oxide with a particle size range of 3 nm to 50 nm;
  • the composite method between titanate nanotubes and nano-tantalum oxide includes in-situ embedded composite, and the composite nano-metal oxide intermediate product does not contain three-dimensional Continuous network-like nanoporous structure or porous skeleton structure;
  • the composite nanometal oxide intermediate product composed of the above Ta-containing intermediate product and the titanate nanotube intermediate product is heat-treated at 1000°C for 2 hours to obtain a composite nanometal oxide composed of crystalline nanoparticle tantalum oxide and rutile crystalline TiO2 rods.
  • the outer diameter of the rutile crystalline TiO2 rod ranges from 6nm to 25nm, and the long diameter is greater than 3; the particle size range of the crystalline nanotantalum oxide ranges from 3nm to 50nm; the difference between the rutile crystalline TiO2 rod and the nanotantalum oxide
  • the composite methods include in situ embedded composite.
  • This embodiment provides a method for preparing a composite nanometal oxide containing Nb, Zr, Hf and Ti elements and containing titanate nanotubes, including the following steps:
  • the nominal ratio of Zn 75 Ti 5 Hf 5 Zr 5 Nb 5 Mn 5 (atomic percentage) is to weigh the raw materials of gold Zr, Hf, Ti, Nb, Mn, and Zn, and smelt to obtain the composition of Zn 75 Ti 5 Hf 5 Zr 5 Nb 5 Mn 5 alloy melt, and then prepare the alloy melt into an initial alloy strip with a thickness of ⁇ 25 ⁇ m through a copper roller strip rapid solidification method. Its phase composition is mainly composed of Zn and Zr, Hf, Ti, Nb, Mn composed of intermetallic compounds.
  • the composite composite nano-metal oxide intermediate product containing Zr, Hf, Ti, Nb, Mn and other elements is heat-treated at 1000°C for 2 hours to obtain a completely crystalline state through the oxidation of Zr, Hf, Ti, Nb, Mn and other elements.
  • the molar ratio between components corresponding to different metal elements is approximately an equimolar ratio.
  • the method of compounding between components corresponding to different metal elements includes in-situ embedded composite, which includes in-situ embedded composite. In-situ embedded composite at the atomic or atomic cluster scale or in-situ embedded composite at the fine-phase scale.
  • This solution eliminates the need to separately prepare the oxides of these metal elements and then mix them. Instead, the ratio of each metal can be designed during the alloy design. Through this ratio, the content of the corresponding oxides of each metal can be calculated.
  • a partially crystallized composite nanometal oxide intermediate product composed of oxides of Zr, Hf, Ti, Nb, Mn and other elements can be obtained; the atom/atom group process is carried out during the preparation process. In-situ embedded composite at cluster scale or fine phase scale; through further heat treatment, fully composite multi-component composite nano-metal oxides can be obtained.
  • This embodiment provides a composite nanometal oxide containing Cr and Ti elements and a preparation method thereof, which includes the following steps:
  • an alloy melt mainly composed of Al 61 Cr 35 Ti 4 is obtained by smelting Al, Cr and Ti raw materials, and the alloy melt is quickly solidified through a copper roller.
  • the method is used to prepare an initial alloy strip with a thickness of 20 ⁇ m to 30 ⁇ m and a composition mainly composed of Al 61 Cr 35 Ti 4.
  • Its solidification structure is mainly composed of Al 8 Cr 5 (Ti) intermetallic compounds with Ti dissolved in it.
  • the hydrogen evolution and Al removal reaction ends within 10 seconds. After 10 seconds, put the sealed container and reaction system into cooling water and quickly cool it to near room temperature, and at the same time reduce the pressure in the sealed container to normal pressure;
  • Composite nano-metal oxide intermediate product composed of nano-Cr hydroxide or nano-Cr oxide; its morphology is colloidal floc, and the particle size of the floc microstructure is 0.5nm-25nm. Due to the relative Ti content in the initial alloy relative to the Cr content Less often, Ti-containing intermediate products do not appear in the form of titanate or titanate films. They mainly exist in low-crystalline nano-Cr hydroxide or nano-Cr oxide intermediates through in-situ embedded composite.
  • the shape of the original alloy powder before and after the reaction is roughly unchanged, and it is still the original broken and angular powder particles, and its microstructure does not undergo nano-fragmentation, nor does it form A large number of dispersed nano-oxide powders instead generate coarse powder particles composed of a nano-porous network structure that retain the original edges and corners.
  • the particle size is still equivalent to the particle size of the initial alloy powder, which is several microns or tens of microns. Therefore, the reaction between the initial alloy and the alkali solution that occurs at a lower temperature is completely different from the reaction that occurs at a higher temperature, especially preferably near the boiling point of the present invention, and the morphology of the product is also completely different.
  • This comparative example provides a method for preparing nano-ZrO 2 powder, which includes the following steps:
  • the TEM morphology photos and diffraction spectra of oxidized Zr are shown in Figures 21-22. It can be seen that it is mainly in a low crystalline state, and its morphology is mainly colloidal floc.
  • the particle size of the flocculent microstructure is 0.5nm-5nm. .
  • the above-mentioned low crystallinity nano-Zr hydroxide is heat-treated at 900°C for 2 hours to obtain crystalline nano-ZrO 2 .
  • Its TEM morphology photos and diffraction spectra are shown in Figure 25-26; the crystalline nano-ZrO 2 obtained after heat treatment
  • ZrO 2 is a polycrystalline particle, its sintering agglomerates into solid large particles, completely losing the looseness of the particles and showing a low specific surface area. Therefore, this structure is difficult to crush and refine through subsequent ball milling and sanding processes.

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Abstract

一种复合纳米金属氧化物及复合氧化物陶瓷的制备方法。通过含有Al/Zn及目标多金属元素的金属间化合物为初始合金，在一定碱浓度与温度条件下通过析氢脱Al/Zn反应使初始合金纳米碎化，并经进一步形状与成分重组实现了多组元复合纳米金属氧化物的制备。制备方法具有反应时间短、工艺简单、易于操作、成本低的特点，所制备的多种复合纳米金属氧化物材料，在复合材料、催化材料、陶瓷材料、耐火材料、先进电子材料、电池材料、变色材料、吸波材料、污水降解材料、杀菌材料、涂料、颜料、热喷涂材料、传感器等领域均有很好的应用前景。

Description

一种复合纳米金属氧化物及其制备方法与用途 技术领域
本发明涉及纳米材料技术领域，特别是涉及一种复合纳米金属氧化物及复合氧化物陶瓷的制备方法。
背景技术
纳米金属氧化物常用的制备方法是在可溶性金属盐溶液中加碱沉淀法，经过过滤、干燥、煅烧，得到纳米粉体。但由于这种方法生成的沉淀产物大多是胶状氢氧化物，过滤时间长，相应地增加了生产周期；再者沉淀物之间易形成氢键，在过滤、干燥、高温煅烧时易导致粉体颗粒团聚、长大，很难获得颗粒均匀、分散性好、无硬团聚的粉体。
传统方法制备的复合纳米金属氧化物一般采用混粉的方法制备，不同组分在制备步骤上至少需要分别进行，过程繁琐。而且，混粉后各个组分之间一般通过物理吸附或者简单混合的方式复合在一起，这种混合往往难以达到足够均匀的效果。但是，在某些应用领域，需要各组分之间尽可能地混合均匀，甚至需要原位复合才能实现各个组分之间的特殊交互作用，以获得特殊优异的性能。因此，亟待开发出一种通过一个制备过程实现不同氧化物组分之间可以原位复合的复合纳米金属氧化物的新方法。
发明内容
基于此，有必要针对上述问题，提供一种工艺简单、条件温和且适合大规模生产的复合纳米金属氧化物的制备方法，所制备产物不同组分之间可以彼此原位嵌生复合。本发明包含其一至其十二共十二个方面：
其一方面，一种复合纳米金属氧化物的制备方法，其特征在于，包括如下步骤：
步骤一，提供初始合金，所述初始合金的成分组成包含T类元素与A类元素，其中T类元素包含Al、Zn中的至少一种；A类元素包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；其中，M类子元素包含Cr、V、Nb、Ta、W、Mo、Mn、Y、La、Ce、Pr、Nd、Pm、Sm、Eu、Gd、Tb、Dy、Ho、Er、Tm、Yb、Lu中的至少一种；D类子元素包含Zr、Hf中的至少一种；所述初始合金的成分组成主要为A xT y，其中x，y为对应各类元素的原子百分比含量，且5≤x≤55％，45％≤y≤95％；所述初始合金的凝固组织主要由A-T金属间化合物组成；
步骤二，将所述初始合金与碱溶液发生析氢脱T反应，通过控制碱溶液的温度T 1与浓度C 1，使反应过程中反应界面以不低于2μm/min的平均速率由初始合金表面向内推进；
当初始合金中不含D类子元素时，初始合金与所述碱溶液通过析氢脱T反应发生纳米碎化，并经形状与成分重构生成形状在三维方向上至少有一维的尺度不超过500nm的含M与Ti的固态物质；
当初始合金中含D类子元素时，初始合金与所述碱溶液通过析氢脱T反应发生纳米碎化，并经形状与成分重构生成形状在三维方向上至少有一维的尺度不超过500nm的含M或(与)Ti的固态物质；同时，D类子元素在高反应速率对应的碱浓度与温度情况下主要溶于所述碱溶液中，或在相对较低反应速率对应的碱浓度与温度情况下经形状与成分重构主要生成含D的固态物质；
步骤三，析氢脱T反应结束后，
当初始合金中不含D类子元素时，收集所述反应体系中的含M与Ti的固态物质，即得到含M与Ti的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；且所述含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；其中，含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含M中间产物与含Ti中间产物两者之间至少有一个是相；
当初始合金中含D类子元素，且D类子元素主要以含D固态物质存在时，收集所述反应体系中的所有固态物质，即得到由含D中间产物与含M或(与)Ti中间产物组成的复合纳米金属氧化物中间产物，其形状在三维方 向上至少有一维的尺度不超过500nm；且含D中间产物、含M中间产物、含Ti中间产物之间彼此复合的方式包括原位嵌生复合；其中，含D中间产物、含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含D中间产物、含M中间产物、含Ti中间产物三者之间至少有一个是相；
当初始合金中含D类子元素，且D类子元素主要溶于所述碱溶液中时，将液体加入步骤二所述反应体系中，使碱溶液的浓度降低至固态絮状氢氧化D可以析出的浓度C 2以下，析出的固态絮状氢氧化D与之前形成的含M或(与)Ti的固态物质混合，收集所有固态物质，即得到由纳米氢氧化D与含M或(与)Ti中间产物组成的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；其中，C 2<C 1，且当所述复合纳米金属氧化物中间产物中同时包括含M中间产物与含Ti中间产物时，含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；其中，含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含M中间产物与含Ti中间产物两者之间至少有一个是相；
步骤四，将步骤三所述复合纳米金属氧化物中间产物进行热处理，即得到晶化程度提高的复合纳米金属氧化物；其包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；且Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相的尺度进行异类元素对应氧化物的复合。
所述步骤一中，
进一步地，所述M包含Cr、V、Nb、Ta、W、Mo、Mn、Y、Gd中的至少一种；
进一步地，T包含Al；进一步地，T包含Zn；
进一步地，19≤x≤55％，45％≤y≤81％；
进一步地，所述初始合金中的A类元素组成包括如下四种组合中的任意一种：
1)Ti元素、M类子元素；2)D类子元素、M类子元素；
3)D类子元素、Ti元素；4)D类子元素、Ti元素、M类子元素；
进一步地，所述A类元素中，D类子元素、Ti元素、M类子元素这三类子元素中，占主导含量地位的子类元素在A类元素中的摩尔百分比含量低于99％；举例来说，当A类元素由Nb与Ti组成，且Nb占主导含量地位时，Nb在Nb与Ti的总含量中的摩尔占比需要低于99％；
进一步地，所述占主导含量地位的子类元素在A类元素中的摩尔百分比含量低于95％；
进一步地，所述占主导含量地位的子类元素在A类元素中的摩尔百分比含量低于90％；
进一步地，所述占主导含量地位的子类元素在A类元素中的摩尔百分比含量低于80％；
进一步地，D类子元素在A类元素中的摩尔百分比高于30％；进一步地，D类子元素在A类元素中的摩尔百分比高于60％；进一步地，D类子元素在A类元素中的摩尔百分比高于90％；
进一步地，M类子元素在A类元素中的摩尔百分比高于30％；进一步地，M类子元素在A类元素中的摩尔百分比高于60％；进一步地，M类子元素在A类元素中的摩尔百分比高于90％；
进一步地，Ti在A类元素中的摩尔百分比高于30％；进一步地，Ti在A类元素中的摩尔百分比高于60％；进一步地，Ti在A类元素中的摩尔百分比高于90％；
近一步地，所述初始合金的凝固组织主要由A-T金属间化合物组成；其中，A-T金属间化合物为单相金属间化合物或多相金属间化合物；且当A-T金属间化合物为多相金属间化合物时，其包括Ti-T金属间化合物、M-T金属间化合物、D-T金属间化合物，(M-D)-T金属间化合物，(Ti-D)-T金属间化合物，(Ti-M)-T金属间化合物，(Ti-M-D)-T金属间化合物中的至少两种；
且当A-T金属间化合物为单相金属间化合物时，其为(M-D)-T金属间化合物，(Ti-D)-T金属间化合物，(Ti-M)-T金属间化合物，(Ti-M-D)-T金属间化合物中的一种；
进一步地，所述初始合金中，A-T金属间化合物具体的相组成方式不限，只要确保A类元素存在于A-T金属间化合物中即可，即A类元素原子在初始合金中分散分布，且与T类元素原子相邻排列；或者只要确保初始合金中不含有由A类元素组成的A相(A相中A类元素原子在初始合金中聚集排列)即可；
进一步地，所述初始合金通过将含有T类元素与A类元素的合金熔体凝固制备，在合金凝固过程中形成主要由A-T金属间化合物组成的凝固组织；
进一步地，所述初始合金中不包含T相；所述T相，即主要由T类元素组成的相；
进一步地，所述初始合金熔体凝固的速率为0.01K/s～10 8K/s；
进一步地，所述初始合金熔体凝固的速率为1K/s～10 8K/s；
进一步地，所述初始合金的形状包括颗粒状、丝状、条状、带状、片状中的至少一种；
进一步地，所述初始合金的形状在三维方向上任一维度的平均尺寸均大于4μm；
进一步地，所述初始合金的形状在三维方向上任一维度的平均尺寸均大于10μm；
进一步地，所述初始合金的形状在三维方向上任一维度的平均尺寸均大于15μm；
进一步地，当所述初始合金为条带状时，可以通过包括熔体甩带法的方法制备；
进一步地，当所述初始合金为颗粒状时，可以通过铸造法制备体积较大的初始合金铸锭，然后将其破碎成初始合金颗粒。
所述步骤二中，
进一步地，所述碱溶液包含NaOH、KOH、LiOH、RbOH、CsOH、Ba(OH) 2、Ca(OH) 2、Sr(OH) 2溶液中的至少一种；
进一步地，所述碱溶液中的溶剂包含水；作为优选，所述碱溶液中的溶剂为水；
进一步地，所述C 1的范围为4～30mol/L；作为优选，所述C 1的范围为5～15mol/L；作为优选，所述C 1的范围为7～15mol/L；
进一步地，所述与初始合金反应的碱溶液中的碱为过量剂量，碱溶液的体积为初始合金体积的5倍以上，从而可以使得反应一直在较高的碱浓度下进行；
进一步地，所述碱溶液的体积为初始合金体积的10倍以上；
进一步地，所述碱溶液的体积为初始合金体积的20倍以上；
进一步地，一定的碱浓度C 1条件下，所述碱溶液的温度只要能够保证析氢脱T反应过程中反应界面以不低于2μm/min的平均速率由初始合金表面向内推进，且反应过程中初始合金可以通过析氢脱T反应发生纳米碎化即可，即通过析氢脱T反应速率或析氢脱T反应时间(反应速率与初始合金尺寸确定，则反应时间即确定)与反应效果来确定需要的碱溶液的温度T 1。因此，当采用反应速率的值限定反应条件后，也就同时间接地限定了碱溶液的温度T 1值与浓度值范围，即温度T 1与浓度C 1的值可不做具体限制，而是直接通过满足析氢脱T反应过程中反应界面以不低于2μm/min的平均速率进行的T 1与C 1组合为准。
进一步地，2μm/min的平均速率即为反应过程中初始合金可以通过析氢脱T反应发生纳米碎化的临界反应速率；
进一步地，所述发生纳米碎化，是指初始合金经析氢脱T反应碎化成三维方向上至少有一维的尺度小于500nm的单个中间产物或产物；
进一步地，所述发生纳米碎化，是指初始合金经析氢脱T反应碎化成三维方向上至少有一维的尺度小于250nm的单个中间产物或产物；
进一步地，所述T 1≥60℃；进一步地，所述T 1≥80℃；进一步地，T 1>100℃；
进一步地，所述初始合金与碱溶液的反应在常压或高压下进行；
进一步地，所述初始合金与碱溶液的反应在密闭容器内进行；
在密闭容器下，当容器内的压力超过一个大气压力，即为高压；同时，如果容器内反应产生的气体不能排出，也能形成额外高压。
进一步地，在密闭容器内进行反应时，初始合金与碱溶液首先在密闭容器内分开放置，当碱溶液温度达到设定的反应温度时，再将初始合金与碱溶液接触，进行反应。
进一步地，在密闭容器内，碱溶液的温度可以超过其常压下的沸点温度；
进一步地，100℃<T 1≤T f溶液，所述初始合金与碱溶液的反应在常压下进行；其中，T f溶液为常压下所述参与反应的碱溶液的沸点温度；进一步地，所述常压，是指不使用密闭容器情况下的大气环境气压；
进一步地，所述反应在常压环境下进行，常压一般指1个标准大气压，此时对应水的沸点为100℃；当水中溶有碱时，1个标准大气压下碱的水溶液的沸点温度要高于100℃，且碱的浓度越高，则其沸点越高。例如， 摩尔浓度5mol/L的NaOH溶液，沸点T f溶液约为108℃；摩尔浓度7mol/L的NaOH溶液，沸点T f溶液约为112℃；摩尔浓度10mol/L的NaOH溶液，沸点T f溶液约为119℃；摩尔浓度12mol/L的NaOH溶液，沸点T f溶液约为128℃；摩尔浓度15mol/L的NaOH溶液，沸点T f溶液约为140℃；摩尔浓度17mol/L的NaOH溶液，沸点T f溶液约为148℃；摩尔浓度20mol/L的NaOH溶液，沸点T f溶液约为160℃；摩尔浓度25mol/L的NaOH溶液，沸点T f溶液约为180℃；摩尔浓度10mol/L的KOH溶液，沸点T f溶液约为125℃；摩尔浓度12mol/L的KOH溶液，沸点T f溶液约为136℃；摩尔浓度15mol/L的KOH溶液，沸点T f溶液约为150℃；
进一步地，101℃≤T 1≤T f溶液；进一步地，105℃≤T 1≤T f溶液；
进一步地，101℃≤T f溶液-5℃≤T 1≤T f溶液；进一步地，101℃≤T f溶液-2℃≤T 1≤T f溶液；
作为进一步优选，所述碱溶液的温度为T f溶液，即T 1＝T f溶液；
由于反应溶液在常压下所能加热到的最高温度为其沸点温度(T f溶液)，当温度达到该温度后，继续加热，溶液的温度也不会升高，只会沸腾。而要想提高反应温度时，则可通过提高碱溶液的浓度，从而获得更高的沸点温度；因此，沸点温度的控制最为容易、简单、精确。而且，同等浓度下，沸点温度反应所需的反应时间也比沸点以下其它温度反应所需反应时间更短；产物产率与效率也更高。
T类元素包含Al、Zn中的至少一种，而Al、Zn为两性金属，其可以和碱溶液反应变成盐从而溶于碱溶液中，因此可以通过T类元素与碱溶液的反应脱除初始合金中各金属间化合物中的T类元素；
进一步地，所述析氢脱T反应的特征为：初始合金中的T类元素溶解进入溶液，同时析出氢气；
进一步地，所述析氢脱T反应的剧烈成程度与单位时间内反应界面由初始合金表面向内的反应推进速率有关，T 1与C 1的值越高，反应界面推进速率越快，反应越剧烈。
例如，当NaOH浓度为10mol/L时，主要由(TiNb)Al 3金属间化合物组成的初始合金与碱溶液反应过程中，反应界面由初始合金表面向内的推进速率如下：
60℃≤T 1≤80℃时，所述反应界面的平均推进速率约为2μm/min～7μm/min；
80℃≤T 1≤90℃时，所述反应界面的平均推进速率约为7μm/min～15μm/min；
90℃<T 1≤100℃时，所述反应界面的平均推进速率约为15μm/min～30μm/min；
100℃<T 1≤110℃时，所述反应界面的平均推进速率约为30μm/min～50μm/min；
110℃<T 1<119℃时，所述反应界面的平均推进速率约为50μm/min～120μm/min；
T 1＝T f溶液时，所述反应界面的平均推进速率大于120μm/min；
进一步地，所述反应过程中反应界面以不低于7μm/min的平均速率由初始合金表面向内推进；
进一步地，所述反应界面以不低于15μm/min的平均速率由初始合金表面向内推进；
进一步地，所述反应界面以不低于30μm/min的平均速率由初始合金表面向内推进；
进一步地，所述析氢脱T反应过程中施加超声，通过超声处理进一步增进纳米碎化效果与反应速率；
进一步地，所述超声的频率为20kHz～10 6kHz；
进一步地，一定的碱浓度C 1条件下，所述碱溶液的温度T 1只要能够保证析氢脱T反应过程中反应界面以不低于2μm/min的平均速率由初始合金表面向内推进，且反应过程中初始合金可以通过析氢脱T反应发生纳米碎化即可。因此，不同初始合金条件或碱溶液条件下，析氢脱T反应过程中反应界面以不低于2μm/min进行时，所需要的反应溶液温度可能低于60℃；尤其当辅以超声处理时，所需要的反应溶液温度可能更低；
所述初始合金在与碱溶液进行析氢脱T反应的过程中，Ti元素、M类子元素、D类子元素具有不同的中间产物演化与形成趋势：具体来说，
Ti元素经形状与成分重构演化后有生成纳米钛酸盐中间产物的趋势；进一步地，所述含Ti中间产物主要为纳米钛酸盐；进一步地，所述纳米钛酸盐的形状主要为薄膜状，其厚度为0.5nm-5nm，且薄膜的平均面积大于100nm 2；进一步地，所述纳米钛酸盐中的阳离子对应于反应体系碱溶液中的阳离子；如反应体系的碱溶液为NaOH时，所述钛酸盐即为钛酸纳；
M类子元素经形状与成分重构演化后有生成纳米氧化M中间产物的趋势；进一步地，所述含M中间产物主要为纳米氧化M；进一步地，所述纳米氧化M的形状包括薄膜状、颗粒状、板片状、条状、管棒状、团絮状中的至少一种；所述团絮状是指极其细小且没有明显棱角的微结构团聚在一起的状态。进一步地，所述纳米氧 化M的形状在三维方向上至少有一维的尺度不超过500nm；
进一步地，所述纳米氧化M包括低结晶度的纳米氧化M、晶态纳米氧化M、水合纳米氧化M中的至少一种；所述低结晶度纳米氧化M包括非晶态的纳米氧化M；由于纳米氢氧化M可以看做是纳米氧化M与H 2O的结合体，通过较低的温度进行加热脱水即可得到纳米氧化M，因此所述水合纳米氧化M即为纳米氢氧化M；
进一步地，所述纳米氧化M中不同价态的M对应于不同的纳米氧化M；如氧化Mn可以为MnO，也可以为MnO 2；
D类子元素(Zr、Hf元素)在高反应速率对应的碱浓度与温度情况下有溶于所述碱溶液中的趋势；
D类子元素(Zr、Hf元素)在相对较低反应速率对应的碱浓度与温度情况下经形状与成分重构演化后有生成含D固态物质的趋势，且这种含D固态中间产物包括固态纳米氢氧化D与固态DO 2中的至少一种；
进一步地，所述高反应速率为反应平均速率大于15μm/min；
进一步地，所述相对较低反应速率为反应平均速率小于15μm/min；
进一步地，所述含D固态中间产物的形状在三维方向上至少有一维的尺度不超过500nm；
进一步地，当反应在常压下进行，碱溶液为热碱溶液(如T 1>100℃)，尤其在热碱溶液沸点温度T f溶液发生时，D类子元素的溶解现象最为明显。
所述D类子元素的溶解，就是单纯的D-T金属间化合物可以溶于较高反应速率对应的一定温度与浓度的碱溶液中，获得澄清透明的溶液；这是D类元素通过D-T金属间化合物参与析氢脱T反应最独特的现象。
需要说明的是：上述所述中间产物的演化与形成趋势，均是相应的A类元素(Ti元素、M类子元素、D类子元素)中各类子元素摩尔百分含量(见步骤一)占主导地位时显示的特征与趋势；当某一类子元素摩尔百分含量不占主导地位时，由于各子类元素对应的各中间产物在形成过程中的相互影响，其可能不表现出其占主导地位时的演化与形成趋势。
进一步地，所述占主导，是指A类元素(Ti元素、M类子元素、D类子元素)中各类子元素摩尔百分含量占比超过60％的情形。进一步地，所述占主导，是指A类元素(Ti元素、M类子元素、D类子元素)中各类子元素摩尔百分含量占比超过75％的情形。
例如，如果A类元素中，Ti:Nb＝90:10，Ti摩尔比为90％时，A-T金属间化合物析氢脱T反应经形状与成分重构演化后有生成二维薄膜状纳米钛酸盐的趋势；由于Nb含量较少，其可能不表现出其占主导地位时的演化与形成趋势，即其可能不生成独立分散的纳米氧化M，而是直接原位嵌生在二维薄膜状纳米钛酸盐中；这种原位嵌生，包括以原子或原子团簇原位嵌生的方式(Ti与M共处于纳米钛酸盐中，M可以认为是固溶元素)，或以纳米氧化M颗粒的原位嵌生方式。当Ti:Nb＝50:50，则Ti与Nb均不占主导，A-T金属间化合物析氢脱T反应经形状与成分重构演化后生成的中间产物可能继续遵循各自占主导时的演化趋势，也可能因为均具有较高含量的Ti与Nb的相互影响，Ti与Nb均不再遵循各自占主导时的演化趋势，而是呈现全新的演化趋势。
特别地，当上述这种各子类元素不占主导的情况出现时，恰好体现了本申请其一方面各个步骤，以及后续其它几个方面制备复合纳米金属氧化物的巨大优势：因为复合纳米金属氧化物的性能的关键在于最终制备产物的性能，当各子类元素之间在析氢脱T过程中产生极大的交互作用影响并改变各自占主导时的演化形成趋势，就可以获得别的方法不可能获得的均匀复合；这种均匀复合的状态在其一方面步骤二所述过程中存在后，会在其一方面步骤三与步骤四所对应制备过程中一直存在并产生影响(其三方面与其四方面不再重复说明)；且这种均匀复合不仅体现在物理混合均匀方面，还可体现在化学均匀复合方面，如生成全新的单相复合物质，其同时包括两到三个子类元素并在原子或原子团簇尺度均匀分布，如新复合成的单相纳米氧化Ti/M，其既不同于单相纳米氧化Ti，也不同于单相纳米氧化M；这种特殊的复合，可以使得最后获得的复合纳米金属氧化物获得极为优异的性能。因此，本申请不仅其一方面，而且后续其它几个方面关于A-T金属间化合物析氢脱T反应生成的含Ti中间产物、含M中间产物、含D中间产物的特征描述，均是各个组分占主导地位时的特征。当各组分不占主导地位时，可能各自满足上述趋势与特征，也肯能各自不满足上述趋势与特征。但不满足上述趋势与特征的情况，不论生成的新产物是什么，其形貌怎样，都恰好满足了复合更均匀、更彻底的特征，有利于获得性能更为优异的复合纳米金属氧化物及后续制品。
当初始合金中不含D类子元素时，初始合金与所述碱溶液通过析氢脱T反应发生纳米碎化，并经形状与成分重构生成形状在三维方向上至少有一维的尺度不超过500nm的含M与Ti的固态物质，
进一步地，所述含M与Ti的固态物质主要为纳米氧化M与纳米钛酸盐组成的复合物；所述含M、含Ti固态物质的特征详见上述各中间产物演化与形成趋势部分所述；
当初始合金中含D类子元素时，初始合金与所述碱溶液通过析氢脱T反应发生纳米碎化，并经形状与成分重构生成含M或(与)Ti的固态物质；同时，D类子元素在高反应速率对应的碱浓度与温度情况下主要溶于所述碱溶液中，或在相对较低反应速率对应的碱浓度与温度情况下经形状与成分重构主要生成含D的固态物质；所述含M、含Ti、含D固态物质的特征详见上述各中间产物演化与形成趋势部分所述；
进一步地，在含M或(与)Ti的固态物质形成的同时，由于原A-T金属间化合物中，D类子元素与M类子元素及Ti元素往往在原子尺度均匀分布在同一个相里，如Al 3(TiZr)相。因此，含M或(与)Ti的固态物质形成的同时，不可避免地有少部分D类子元素被限制在其中，从而在先形成的含M或(与)Ti的固态物质中就有了少量D类子元素参与的复合；而大部分D类子元素则溶解于碱溶液中；
进一步地，所述发生纳米碎化，是指反应界面的初始合金经析氢脱T反应碎化，同时经形状与成分重构生成纳米尺度的含M或(与)Ti的固态物质；在这个过程中，析氢脱T反应剧烈释放的氢气促进了中间产物及产物的纳米碎化、以及产物离开反应界面后在碱溶液中的扩散分布。
进一步地，所述纳米碎化后，碎化后的含M或(与)Ti的固态物质中不含有三维连续网络状的纳米多孔结构或多孔骨架结构；
进一步地，所述含M或(与)Ti的固态物质的大小小于发生纳米碎化之前的初始合金大小的0.25倍；
进一步地，所述含M或(与)Ti的固态物质的大小小于发生纳米碎化之前的初始合金大小的0.05倍；
无论是条带状还是破碎成粉末状的初始合金，由于技术水平的限制，其厚度或者粒度一般至少为数微米级，如5μm以上；而含M或(与)Ti的固态物质的粒径或厚度大小不超过500nm，表明其经过了充分地纳米碎化过程。
进一步地，所述形状重构，是指析氢脱T反应得到的纳米尺度的含M或(与)Ti的固态物质，不是简单的对纳米多孔结构(ligament)的物理碎化，而是发生除了物理碎化之外的形状变化。
一般来说，传统的室温附近发生的浓碱脱合金反应，反应前后，产物相对于初始合金的大致形状不发生明显改变；如初始合金为带有棱角的颗粒状时，传统脱合金产物一般仍为带有原棱角形状的纳米多孔颗粒状；而本申请所述含M或(与)Ti的固态物质的形状与初始合金的形状完全不同，其形状发生了极大的变化；
进一步地，所述初始合金与碱溶液在一定的温度与浓度下反应，且保证反应速率不低于2μm/min，对于通过纳米碎化及形状与成分重构生成含M或(与)Ti的固态物质非常重要。在对比实施例1中，常压下，当含有(NbTi)Al 3金属间化合物的初始合金粉末与10mol/L且为25℃的NaOH溶液反应2h，反应前后的原初始合金粉末的形状大致不变，仍然为原破碎状且具有棱角的粉末状颗粒，且其微观结构上也不生成大量分散的诸如纳米颗粒、纳米片或者纳米棒等产物，而是生成纳米多孔结构，且这种纳米多孔结构通过三维网状链接的方式构成与原合金粉末形状一致的外观形貌，其粒径大小仍然为初始合金粉末相当的大小，主要为数微米或者数十微米级。因此，室温附近较低温度下所发生的初始合金与碱溶液的反应与本发明在较高温度，如T 1>100℃的温度区间，尤其是碱溶液沸点温度附近的反应完全不同，产物形貌也完全不同。
所述步骤三中，
析氢脱T反应结束所需时间可以通过氢气析出是否结束来判断，当肉眼观察不到反应产生的气体析出时，可以认为析氢脱T反应完成。
除了碱浓度与碱溶液温度，初始合金中T类元素通过析氢脱T反应被完全脱除的反应时间还与初始合金的形状相关：当初始合金粉末颗粒越小，或初始合金条带越薄时，析氢脱T反应完成所需的时间越短；反之，析氢脱T反应完成所需的时间越长。根据反应界面的平均推进速率以及初始合金的尺寸，即可计算出析氢脱T反应完成所需最少的反应时间t。例如，当初始合金为厚度为d的条带状，且反应界面的平均推进速率为v时，考虑到反应界面分别从条带上下两个面推进，t＝0.5d/v；同理，当初始合金为直径为d的颗粒状，且反应界面的平均推进速率为v时，t＝0.5d/v。
在某一个实施例中，含有(NbTi)Al 3金属间化合物的初始合金条带与10mol/L且为沸点温度的NaOH溶液反应(沸点温度约119℃)，初始合金条带反应界面推进的平均速率约为～120μm/min，亦即40μm厚的初始合金 条带，10s就可以完成析氢脱Al反应；20μm厚的初始合金条带，5s就可以完成析氢脱Al反应；即使5mm粒径的初始合金粗颗粒，21min就可以将其析氢脱Al反应完毕；考虑到条带或粉末粒径可能的不均匀，存在较厚的条带或较大的颗粒，实际反应过程可以稍延长一点时间，以确保初始合金反应完毕并进行下一步操作。
进一步地，所述析氢脱T的反应时间为10s～59min；进一步地，所述析氢脱T的反应时间为10s～29min；进一步地，所述析氢脱T的反应时间为10s～9.9min；进一步地，所述析氢脱T的反应时间为10s～4.9min；进一步地，所述析氢脱T的反应时间为10s～1min；进一步地，所述析氢脱T的反应时间为10s～30s；
当析氢脱T反应完成后，继续延长反应体系在原反应温度的保温时间，仍然能保证产物为具有颗粒分散性的纳米级产物，但保温时间足够长时，产物的形貌可能会发生一定的变化。也就是说，当初始合金与碱溶液的反应时间远超过所需最短析氢脱T反应时间t，如达数小时时，仍能够获得含M或(与)Ti的固态物质，但是其形貌可能发生一定的变化。
当初始合金中不含D类子元素时，收集所述反应体系中的含M与Ti的固态物质，即得到含M与Ti的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；且所述含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；其中，含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含M中间产物与含Ti中间产物两者之间至少有一个是相。如，当含M中间产物为原子或原子团簇时，其不形成含M的相，则其以原子或原子团簇的方式存在于含Ti中间产物相中。
所述相，也可以是低结晶度的相，也可以是高结晶度的相，但其必定是固态的相，如低结晶度氢氧化Zr相，高结晶度氧化Ta相；本申请各个方面与相有关的解释均与此一致。
进一步地，收集所述反应体系中的含M与Ti的固态物质的过程，包括对含M与Ti的固态物质的分离收集，清洗，干燥过程；
进一步地，所述含M与Ti的固态物质的分离收集过程，包括如下a)或b)过程中的任意一种：
a)往反应体系中加入大量冷的溶剂(如水)，使步骤二所述反应体系中含M与Ti的固态物质与碱溶液的温度迅速降低，同时降低反应体系中碱溶液的浓度，然后将稀释与降温后的固液分离；很显然，降低浓度与温度后的碱溶液更加安全，也确保了产物形貌的稳定；
b)将反应体系中热的碱溶液与含M与Ti的固态物质一并通过过滤装置(如过滤网)进行过滤分离，从而降低含M与Ti的固态物质的温度，同时实现固液分离。
进一步地，所述清洗过程包括通过稀酸溶液对含M与Ti的固态物质清洗至PH＝4-8，清洗的作用包括清除所述含M与Ti的固态物质上残留的碱，同时对纳米钛酸盐进行阳离子调整；
作为优选，所述稀酸溶液中氢离子浓度为0.001mol/L～0.1mol/L；
进一步地，当对含M与Ti的固态物质进行稀酸清洗后，含M与Ti的固态物质中的纳米钛酸盐转变为纳米钛酸，即纳米钛酸盐发生H +与钛酸盐阳离子的置换，但转变前后形貌基本不变。进一步地，所述纳米钛酸的形状为二维薄膜状；
进一步地，所述含M与Ti的复合纳米金属氧化物中间产物的组成包含纳米氧化M，同时包含纳米钛酸盐与纳米钛酸中的至少一种；
进一步地，所述纳米钛酸盐薄膜厚度为0.25nm～7.5nm；作为优选，所述纳米钛酸盐薄膜厚度0.25nm～5nm；
作为优选，所述纳米钛酸盐薄膜厚度0.25nm～2nm；
进一步地，所述纳米钛酸盐薄膜的平均面积大于100nm 2；
进一步地，所述纳米钛酸薄膜厚度为0.25nm～7.5nm；作为优选，所述纳米钛酸薄膜厚度0.25nm～5nm；
作为优选，所述纳米钛酸薄膜厚度0.25nm～2nm；
进一步地，所述纳米钛酸薄膜的平均面积大于100nm 2；
进一步地，所述纳米钛酸的化学组成包含H、Ti、O元素；
进一步地，所述纳米钛酸的化学组成包含H 4TiO 4；
进一步地，所述含M与Ti的复合纳米金属氧化物中间产物中，含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合与物理吸附复合；
其中，含M中间产物主要为纳米氧化M，含Ti中间产物主要为纳米钛酸盐；如果经过酸洗后，则含Ti中间产物主要为纳米钛酸；
进一步地，所述含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；
所述原位嵌生，是指原位镶嵌生成的一种形成方式，即含Ti中间产物与含M中间产物相互之间通过部分或全部内生镶嵌的方式结合，不依靠外加或者外混的方式使其分布在彼此之中；部分内生镶嵌是指内嵌的组分其只有部分体积发生内嵌；可以理解，当含Ti中间产物与含M中间产物同时生成时，一定存在含Ti中间产物与含M中间产物彼此部分或全部原位镶嵌情况；
这种原位嵌生是在析氢脱T反应的过程中含Ti中间产物与含M中间产物同时形成的过程中同时内嵌完成的。所述原位，是指含Ti中间产物与含M中间产物同时生成；
这种嵌生与普通的靠范德华力物理吸附主导的其它文献报道吸附结合不同(范德华力吸附的纳米颗粒可以移动、脱落)，其可以保证含Ti中间产物与含M中间产物彼此可以紧密地嵌生在一起(不能移动、脱落)。
这种原位嵌生复合方式，可以保证含M中间产物与含Ti中间产物在制备之时就充分均匀地分散在一起，而且不会发生含M中间产物的团聚与含Ti中间产物的团聚；相比而言，如果分开制备含M中间产物与含Ti中间产物，然后将两者混合，则很难均匀分散；所以，原位嵌生复合不可能发生在分开制备两种组分再混合的情形；
进一步地，关于所述”含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含M中间产物与含Ti中间产物两者之间至少有一个是相”的理解，举例来说：是指含M中间产物在足够小或者足够少时，不足以形成含M中间产物的相结构，则其不以某个相的方式存在，而是以含M的原子或原子团簇存在，虽然这些含M的原子或原子团簇也与O通过某种方式结合，但其大小也不足以形成氧化物相。然而，复合纳米金属氧化物中间产物作为固态存在，其至少需要有一个作为基体的相，因此，当含M中间产物以含M的原子或原子团簇存在时，含Ti中间产物必定需要以作为基体的相的方式存在；该作为基体的主要由含Ti中间产物组成的相，可以是非晶相，也可以是晶态相，也可以是介于两者之间的相；另外一种情况，含M中间产物与含Ti中间产物均为各自对应的相，此种情况很好理解，哪种中间产物体积百分含量高，其即为作为基体的相。
该解释同样适用于当初始合金中含D类子元素时的两种情况；且后续其二方面至其四方面也有类似的表述，其含义其二方面至其四方面不再重复解释。
进一步地，当含M中间产物与含Ti中间产物通过原位嵌生复合成某种接近单一的结构，如含M/Ti的中间产物时，其也属于所述原位嵌生复合的情形。此时，含M中间产物与含Ti中间产物均是具有某种结构的含M/Ti的中间产物，甚至是单一的相(此时，含M中间产物与含Ti中间产物即为同一含M/Ti中间产物)，且其中M或(与)Ti在原子尺度原位嵌生复合，为最彻底的复合；这种情况，可以认为是M以原子或原子团簇方式原位嵌生在含M/Ti的中间产物基体中；也可以认为是Ti以原子或原子团簇方式原位嵌生在含M/Ti的中间产物基体中，因为含M/Ti的中间产物基体为非晶态或低结晶态的情况下，不能判断基体是含Ti中间产物还是含M中间产物,，只能认为其是含M/Ti的中间产物。
进一步地，所述含M中间产物主要为纳米氧化M；
进一步地，所述纳米氧化M中不同价态的M对应于不同的纳米氧化M；如氧化Mn可以为MnO，也可以为MnO 2；
进一步地，所述纳米氧化M包括低结晶度的纳米氧化M、晶态纳米氧化M、水合纳米氧化M中的至少一种；
进一步地，所述低结晶度纳米氧化M包括非晶态的纳米氧化M；
由于纳米氢氧化M可以看做是纳米氧化M与H 2O的结合体，通过较低的温度进行加热脱水即可得到纳米氧化M，因此所述水合纳米氧化M即为纳米氢氧化M；
进一步地，所述纳米氧化M具有颗粒分散性；
进一步地，所述纳米氧化M的形状在三维方向上至少有一维的尺度不超过500nm；
进一步地，所述纳米氧化M的形状在三维方向上至少有一维的尺度不超过250nm；
进一步地，所述纳米氧化M的形状在三维方向上至少有一维的尺度不超过150nm；
进一步地，所述纳米氧化M为相时，其形状包括薄膜状、颗粒状、板片状、条状、管棒状、团絮状中的至少一种；所述团絮状是指极其细小且没有明显棱角的微结构团聚在一起的状态。
进一步地，所述纳米氧化M虽然可以软团聚在一起，但其不通过三维连续刚性网络状结构紧密连接在一起，并维持原初始合金的外形。
进一步地，所述纳米氧化M主要为薄膜状时，其厚度为0.25nm～30nm；且薄膜的平均面积大于100nm 2；
进一步地，所述纳米氧化M主要为颗粒状时，其粒径范围为1.5nm～500nm；优选为1.5nm～200nm；优选为1.5nm～100nm；
进一步地，所述纳米氧化M主要为板片状时，其厚度范围为1.5nm～100nm，优选为5nm～30nm，进一步优选为5nm～20nm；且板片的平均面积大于100nm 2；
进一步地，所述纳米氧化M主要为团絮状时，其团絮微结构的大小为1nm～15nm；
进一步地，所述纳米氧化M主要为管棒状时，其包括管状、棒状，其直径范围为2nm～200nm；进一步优选为2nm～50nm；且其长径比大于2；
说明：上述所述各子类中间产物的特征，均是相应的A类元素(Ti元素、M类子元素)中各类子元素摩尔百分含量占主导地位时显示的特征与趋势；当某一类子元素摩尔百分含量不占主导地位时，由于各子类元素对应的各中间产物在形成过程中的相互影响，其可能不表现出其占主导地位时的演化与形成趋势。
当初始合金中含D类子元素，且D类子元素主要以含D固态物质存在时，收集所述反应体系中的所有固态物质，即得到由含D中间产物与含M或(与)Ti中间产物组成的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；且含D中间产物、含M中间产物、含Ti中间产物之间彼此复合的方式包括原位嵌生复合；其中，含D中间产物、含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含D中间产物、含M中间产物、含Ti中间产物三者之间至少有一个是相。
由步骤二可知，D类子元素(Zr、Hf元素)在相对较低反应速率对应的碱浓度与温度情况下经形状与成分重构演化后有生成含D固态物质的趋势，且这种含D固态中间产物包括固态纳米氢氧化D与固态DO 2中的至少一种；
进一步地，所述含D固态中间产物的形状在三维方向上至少有一维的尺度不超过500nm；
进一步地，所述含Ti中间产物主要为纳米钛酸盐；进一步地，所述纳米钛酸盐为相时，其形状主要为薄膜状，厚度为0.5nm-5nm，且薄膜的平均面积大于100nm 2；进一步地，所述纳米钛酸盐中的阳离子对应于反应体系碱溶液中的阳离子；如反应体系的碱溶液为NaOH时，所述钛酸盐即为钛酸纳；
进一步地，所述含M中间产物主要为纳米氧化M；进一步地，所述纳米氧化M为相时，其形状包括薄膜状、颗粒状、板片状、条状、管棒状、团絮状中的至少一种；所述团絮状是指极其细小且没有明显棱角的微结构团聚在一起的状态。进一步地，所述纳米氧化M的形状在三维方向上至少有一维的尺度不超过500nm；
进一步地，所述各子类中间产物彼此复合的情况包括以下三种中的任意一种：含D中间产物与含M中间产物复合；含D中间产物与含Ti中间产物复合，含D中间产物、含M中间产物、含Ti中间产物三者复合；且所述任意一种复合组合中的复合方式均包括原位嵌生复合；
说明：上述所述各子类中间产物的特征，均是相应的A类元素(Ti元素、M类子元素、D类子元素)中各类子元素摩尔百分含量占主导地位时显示的特征与趋势；当某一类子元素摩尔百分含量不占主导地位时，由于各子类元素对应的各中间产物在形成过程中的相互影响，其可能不表现出其占主导地位时的演化与形成趋势。
当初始合金中含D类子元素时，且D类子元素主要溶于所述碱溶液中时，将液体加入步骤二所述反应体系中，使碱溶液的浓度降低至固态絮状氢氧化D可以析出的浓度C 2以下，析出的固态絮状氢氧化D与之前形成的含M或(与)Ti的固态物质混合，收集所有固态物质，即得到由纳米氢氧化D与含M或(与)Ti的固态物质组成的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；其中，当所述复合纳米金属氧化物中间产物中包括含M中间产物与含Ti中间产物时，含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合。其中，含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含M中间产物与含Ti中间产物两者之间至少有一个是相。
进一步地，由于含M或(与)Ti的固态物质形成的同时，也必然有少部分D类子元素被限制在其中，从而在先形成的含M或(与)Ti的固态物质中也有少量D类子元素参与的复合；
进一步地，所述液体为对应碱溶液的溶剂；
进一步地，所述液体包含水；
进一步的，所述液体的温度为常温；进一步的，所述液体的温度为0℃～40℃；
进一步地，加入液体的过程伴随反应体系碱溶液的充分搅拌，以确保析出的固态絮状氢氧化D尽可能地通过异质形核的方式依附生长在之前形成的含M或(与)Ti的固态物质上，从而实现氢氧化D与含M或(与)Ti的固态物质的均匀混合；
进一步地，C 2的浓度依托效果确定，其值为可以使固态絮状(或称之为胶状)氢氧化D可以析出的浓度；
进一步地，C 2≤3mol/L；进一步地，C 2≤2mol/L；
当反应在常压下进行时，因为反应在敞口容器中进行，因此可以很容易地通过往反应体系中加入冷的液体(如水)，来使步骤二所述反应体系中碱溶液浓度降低至C 2以下，同时将含M或(与)Ti的固态物质及碱溶液的温度同步降低；
进一步地，在接近临界浓度C 2时，通过控制浓度降低的速率，控制固态絮状氢氧化D的析出速率；氢氧化D析出越慢，其越容易与含M或(与)Ti的固态物质均匀混合；
进一步地，接近临界浓度C 2时，浓度降低的速率不超过0.1mol/L每秒；
进一步地，所述稀释的用液体中含有表面活性剂或修饰剂；
所述液体中添加表面活性剂或修饰剂的目的在于：控制析出的纳米氧化D的颗粒大小，抑制其异常合并长大；进一步地，所述表面活性剂或修饰剂包括PVP、CTAB、CTAC中的至少一种；
进一步地，收集所述所有固态物质的过程，包括对所述所有固态物质的分离收集，清洗，干燥过程；
进一步地，所述清洗过程包括通过稀酸溶液对所有固态物质清洗至PH＝4-8，清洗的作用包括清除所述所有固态物质上残留的碱，同时对存在的纳米钛酸盐进行阳离子调整，使其变成纳米钛酸。
进一步地，当对含Ti的固态物质进行稀酸清洗后，含Ti的固态物质中的纳米钛酸盐转变为纳米钛酸，即纳米钛酸盐发生H +与钛酸盐阳离子的置换。进一步地，所述纳米钛酸的形状为二维薄膜状；
进一步地，所述含M中间产物主要为纳米氧化M，含Ti中间产物主要为纳米钛酸盐；如果经过酸洗后，则含Ti中间产物主要为纳米钛酸；
进一步地，所述纳米钛酸盐薄膜厚度为0.25nm～7.5nm；作为优选，所述纳米钛酸盐薄膜厚度0.25nm～5nm；
作为优选，所述纳米钛酸盐薄膜厚度0.25nm～2nm；
进一步地，所述纳米钛酸盐薄膜的平均面积大于100nm 2；
进一步地，所述纳米钛酸薄膜厚度为0.25nm～7.5nm；作为优选，所述纳米钛酸薄膜厚度0.25nm～5nm；
作为优选，所述纳米钛酸薄膜厚度0.25nm～2nm；
进一步地，所述纳米钛酸薄膜的平均面积大于500nm 2；
进一步地，所述纳米钛酸的化学组成包含H、Ti、O元素；
进一步地，所述纳米钛酸的化学组成包含H 4TiO 4；
进一步地，当复合纳米金属氧化物中间产物同时含M与Ti时，所述含M与Ti的复合纳米金属氧化物中间产物的组成包含纳米氧化M，同时包含纳米钛酸盐与纳米钛酸中的至少一种；
进一步地，且当所述复合纳米金属氧化物中间产物中同时包括含M中间产物与含Ti中间产物时，含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合与物理吸附复合；
进一步地，且当所述复合纳米金属氧化物中间产物中同时包括含M中间产物与含Ti中间产物时，含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合。
进一步地，所述纳米氧化M与纳米钛酸盐薄膜复合的方式包括原位嵌生复合；
进一步地，所述纳米氧化M与纳米钛酸薄膜复合的方式包括原位嵌生复合；
进一步地，所述纳米氧化M包括低结晶度的纳米氧化M、晶态纳米氧化M、水合纳米氧化M中的至少一种；
进一步地，所述低结晶度纳米氧化M包括非晶态的纳米氧化M；
由于纳米氢氧化M可以看做是纳米氧化M与H 2O的结合体，通过较低的温度进行加热脱水即可得到纳米氧化M，因此所述水合纳米氧化M即为纳米氢氧化M；
进一步地，所述纳米氧化M具有颗粒分散性；
进一步地，所述纳米氧化M的形状在三维方向上至少有一维的尺度不超过500nm；
进一步地，所述纳米氧化M的形状在三维方向上至少有一维的尺度不超过250nm；
进一步地，所述纳米氧化M的形状在三维方向上至少有一维的尺度不超过150nm；
进一步地，所述纳米氧化M为相时，其形状包括薄膜状、颗粒状、板片状、条状、管棒状、团絮状中的至少一种；所述团絮状是指极其细小且没有明显棱角的微结构团聚在一起的状态。
进一步地，所述纳米氧化M虽然可以软团聚在一起，但其不通过三维连续刚性网络状结构紧密连接在一起，并维持原初始合金的外形。
进一步地，所述纳米氧化M主要为薄膜状时，其厚度为0.25nm～30nm；且薄膜的平均面积大于100nm 2；
进一步地，所述纳米氧化M主要为颗粒状时，其粒径范围为1.5nm～500nm；优选为1.5nm～200nm；优选为1.5nm～100nm；
进一步地，所述纳米氧化M主要为板片状时，其厚度范围为1.5nm～100nm，优选为5nm～30nm，进一步优选为5nm～20nm；且板片的平均面积大于100nm 2；
进一步地，所述纳米氧化M主要为团絮状时，其团絮微结构的大小为1nm～15nm；
进一步地，所述纳米氧化M主要为管棒状时，其包括管状、棒状，其直径范围为2nm～200nm；进一步优选为2nm～50nm；且其长径比大于2；
进一步地，所述纳米氢氧化D主要为低结晶度的纳米氢氧化D；
进一步地，所述纳米氢氧化D为絮状结构，其絮状微结构的尺寸范围为0.5nm～10nm；
说明：所述絮状结构也可称为胶状结构，或胶絮状结构；
所述纳米氢氧化D主要通过物理吸附的复合方式与含M中间产物或(与)含Ti中间产物进行复合。可以理解，因为纳米氢氧化D从溶液中的析出晚于含M中间产物或(与)含Ti中间产物的形成，因此，其主要通过物理吸附的方式与含M中间产物或(与)含Ti中间产物复合；
进一步地，所述纳米氢氧化D主要通过物理吸附的方式与纳米氧化M或(与)纳米钛酸盐薄膜复合；
说明：上述所述各子类中间产物的特征，均是相应的A类元素(Ti元素、M类子元素、D类子元素)中各类子元素摩尔百分含量占主导地位时显示的特征与趋势；当某一类子元素摩尔百分含量不占主导地位时，由于各子类元素对应的各中间产物在形成过程中的相互影响，其可能不表现出其占主导地位时的演化与形成趋势。
进一步地，所述复合纳米金属氧化物中间产物的热稳定性或(与)晶化温度高于相似工艺制备的对应的单一纳米金属氧化物中间产物的热稳定性或(与)晶化温度。这种热稳定性或(与)晶化温度的提高，与不同的A类子元素(元素Ti、M类子元素、D类子元素)在复合纳米金属氧化物中间产物中的特殊复合有关。这种提高热稳定性或(与)晶化温度的复合包括两类：一类是初始原位嵌生复合，包括原子、原子团簇、相尺度的原位嵌生；另一类是纳米氢氧化D对其它中间产物以超细、超高分散性的物理吸附复合，其在后期热处理过程中会诱导出一种烧结嵌生复合。例如，当超细絮状氢氧化D析出时，其均匀吸附在在先析出的纳米氧化M上，虽然两者初始为物理吸附复合，但由于这种物理吸附极为均匀且尺度极小，在后续烧结过程中，通过热处理会诱导一种烧结嵌生复合的状态，导致体积较小的原子或相被烧结长大后的基体相包裹，这种烧结嵌生复合的存在会影响体积占主基体相中的原子扩散重排，从而提高其烧结过程中的热稳定性或(与)晶化温度。上述两类情况，异种组分在极小尺度的复合均会影响基体相原子的扩散重排，从而提高复合纳米金属氧化物中间产物的热稳定性或(与)晶化温度。例如，由元素Ti与M类子元素组成的复合纳米金属氧化物中间产物的热稳定性或晶化温度高于单独由Ti元素或单独由M类元素组成的纳米金属氧化物中间产物的热稳定性或晶化温度。
进一步地，所述复合纳米金属氧化物中间产物中，包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；且所述复合纳米金属氧化物中间产物中，Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相(细小的相的简称)的尺度进行异类元素对应氧化物中间产物的复合；其中，所述原子/原子团簇尺度大小为0.25nm-2.5nm；所述细相的平均粒径低于250nm；
进一步地，所述复合纳米金属氧化物中间产物中，Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相的尺度进行异类元素对应氧化物中间产物的原位嵌生复合。
说明：一般来说，当初始合金中含D类子元素，且D类子元素在高反应速率对应的碱浓度与温度情况下主要溶于所述碱溶液中时，碱溶液浓度降低后D类子元素主要通过氢氧化D析出，并与在先析出的含M中间产 物或(与)含Ti中间产物主要以物理吸附复合。但是，在初始合金中存在D类子元素，同时存在M或(与)Ti类子元素的情况下，析氢脱T反应过程中，在先析出的含M中间产物或(与)含Ti中间产物中也不可避免地存在少量通过原位嵌生复合的含D中间产物。这种情况下，在先析出过程中，少量D类子元素也参与了原位嵌生复合。
进一步地，所述含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合。
进一步地，所述中间产物细相的平均粒径低于125nm；进一步地，所述中间产物细相的平均粒径低于50nm；
进一步地，所述中间产物细相的平均粒径低于25nm；进一步地，所述中间产物细相的平均粒径低于15nm；
所述原子/原子团簇尺度为0.25nm-2.5nm；其中原子尺度为0.25nm-0.5nm，原子团簇尺度为0.5nm-2.5nm；在0.25nm-2.5nm尺度，不足以形成一个中间产物相，只能称之为原子或原子团簇；
作为优选，所述复合纳米金属氧化物中间产物中，Ti元素、M类子元素、D类子元素这三类元素在原子/原子团簇尺度进行异类元素的复合；其中，所述原子/原子团簇尺度大小为0.25nm-2.5nm。
所述步骤四中，
进一步地，所述热处理的温度为300℃～2000℃；进一步地，所述热处理的温度为400℃～2000℃；进一步地，所述热处理的温度为500℃～2000℃；
进一步地，所述热处理时间为1min～24h；进一步地，所述热处理时间为5min～24h；
进一步地，所述热处理时间为30min～24h；
可以理解，随着热处理时间的延长，热处理温度的升高，所得热处理产物的结晶度不断提高，直到全部晶化。
进一步地，所述晶化程度提高的复合纳米金属氧化物中，Ti元素、M类子元素、D类子元素这三类元素在原子/原子团簇尺度或细相(细小的相的简称)的尺度进行异类元素的复合；其中，所述原子/原子团簇尺度大小为0.25nm-2.5nm；所述细相的平均粒径低于250nm；
进一步地，所述Ti元素对应的相为部分晶化或全部晶化的纳米TiO 2；所述M类子元素对应的相为部分晶化或全部晶化的纳米氧化M、所述D类子元素对应的相为部分晶化或全部晶化的纳米DO 2；
进一步地，所述细相的平均粒径低于125nm；进一步地，所述细相的平均粒径低于50nm；
进一步地，所述细相的平均粒径低于25nm；进一步地，所述细相的平均粒径低于15nm；
所述原子/原子团簇尺度为0.25nm-2.5nm；其中原子尺度为0.25nm-0.5nm，原子团簇尺度为0.5nm-2.5nm；在0.25nm-2.5nm尺度，不足以形成一个相，只能称之为原子或原子团簇；
作为优选，所述晶化程度提高的复合纳米金属氧化物中，Ti元素、M类子元素、D类子元素这三类元素在原子/原子团簇尺度进行异类元素的复合；其中，所述原子/原子团簇尺度大小为0.25nm-2.5nm。
进一步地，各A类元素子类元素所对应的相的晶化程度与热处理温度和时间相关；根据相转化规律，当晶化不完全时，部分晶化的纳米TiO 2可能含有钛酸的组分；部分晶化的纳米氧化M可能含有氢氧化M组分；部分晶化的纳米DO 2可能含有氢氧化D的组分。
关于“所述晶化程度提高的复合纳米金属氧化物中，Ti元素、M类子元素、D类子元素这三类元素在原子/原子团簇尺度或细相的尺度进行异类元素的复合；其中，所述原子/原子团簇尺度大小为0.25nm-2.5nm；所述细相的平均粒径低于250nm”的理解：即晶化程度提高的复合纳米金属氧化物中，把Ti元素、M类子元素、D类子元素各自对应的组分单独分开来评判，其尺度较小的组分的粒度要么是原子/原子团簇级别(0.25nm-2.5nm)，要么是平均粒径低于250nm的细相级别。举例来说：如果晶化程度提高的复合纳米金属氧化物为(TiCr)O 2，其为少量Cr以原子或原子团簇嵌入TiO 2形成，则Ti元素、Cr元素(属于M类子元素)在原子/原子团簇尺度进行了异类元素的复合；如果晶化程度提高的复合纳米金属氧化物为ZrO 2相为与氧化Cr相的复合时，则两者中尺度较小的相其平均粒径为低于250nm且大于2.5nm的细相级别。即细相的表述为出现两个或两个以上相的情形，且细相为平均尺度较小的那个相。(该解释适用于本申请所有方面，包括其一至其四方面)
进一步地，所述晶化程度提高的复合纳米金属氧化物中，Ti元素、M类子元素、D类子元素这三类元素在细相的尺度进行异类元素的复合时，复合纳米金属氧化物在热处理过程中的演化规律及产物特征包括如下特征：
当初始合金中不含D类子元素时，所述复合纳米金属氧化物主要为纳米氧化M与纳米TiO 2的复合；且所述纳米氧化M与纳米TiO 2复合的方式包括原位嵌生复合；
当初始合金中含D类子元素时，所述复合纳米金属氧化物主要为纳米DO 2与纳米氧化M或(与)纳米TiO 2的复合；且当所述复合纳米金属氧化物中同时包括纳米氧化M与纳米TiO 2时，纳米氧化M与纳米TiO 2复合的方式包括原位嵌生复合。
进一步地，所述复合纳米金属氧化物中间产物在进行热处理之前稀酸清洗至PH＝4-8，以清除复合纳米金属氧化物中间产物上的残余碱；同时，当复合纳米金属氧化物中间产物中含有纳米钛酸盐时，稀酸清洗可将纳米钛酸盐转变为纳米钛酸；
进一步地，所述纳米DO 2与纳米氧化M或(与)纳米TiO 2的复合，包括三种情况：纳米DO 2与纳米氧化M的复合；纳米DO 2与纳米TiO 2的复合；纳米DO 2与纳米氧化M，及纳米TiO 2的复合；
进一步地，所述纳米氧化M中不同价态的M对应于不同的纳米氧化M；如氧化Mn可以为MnO，也可以为MnO 2；
a)进一步地，所述热处理过程中，随着热处理温度提高，热处理时间提高，所述复合纳米金属氧化物中间产物中的纳米钛酸逐步向锐钛矿型TiO 2转变，然后进一步向金红石型TiO 2转变；
b)进一步地，所述热处理过程中，随着热处理温度提高，热处理时间提高，所述复合纳米金属氧化物中间产物中的纳米氢氧化D逐步向晶态纳米DO 2转变；其中，所述晶态DO 2包括三种情况中的至少一种：ZrO 2，HfO 2，(Zr/Hf)O 2；
c)进一步地，所述热处理过程中，随着热处理温度提高，热处理时间提高，所述复合纳米金属氧化物中间产物中的纳米氧化M逐步向晶态纳米氧化M转变；
上述a)-c)三种情况复合纳米金属氧化物中间产物的转变程度与热处理时间和温度相关。在一定的热处理时间和温度条件下，任何结晶程度(结晶度为0-100％)的产物均是本申请所保护的范围；只要热处理时间足够长，温度足够高，复合纳米金属氧化物中间产物均能完全发生上述a)-c)的转变。
说明：上述所述各子类中间产物在热处理过程中的演化趋势与特征，均是相应的A类元素(Ti元素、M类子元素、D类子元素)中各类子元素摩尔百分含量占主导地位时显示的特征与趋势；当某一类子元素摩尔百分含量不占主导地位时，由于各子类元素对应的各中间产物在热处理过程中的演化趋势与特征相互影响，其可能不表现出其占主导地位时的演化趋势与特征。
进一步地，当复合纳米金属氧化物中间产物原来就是原位嵌生状态，如纳米氧化M与纳米钛酸的原位嵌生复合，其在烧结之前即处于最佳均匀分散状态，则烧结后仍然可以获得最佳的均匀分散状态；
进一步地，所述复合纳米金属氧化物的颗粒疏松性或(与)比表面积高于相似工艺制备的对应的单一纳米金属氧化物的颗粒疏松性或(与)比表面积。该现象产生的原因与上述复合纳米金属氧化物中间产物热稳定性或(与)晶化温度提高的原因类似，均与初始原位嵌生复合或热处理诱导的烧结嵌生复合相关。
相比单一组分纳米金属氧化物热处理后的颗粒疏松性或比表面积，当晶化程度提高的复合纳米金属氧化物的颗粒疏松性或比表面积提高后，其更容易通过后续砂磨、球磨获得更细的晶化程度提高的复合纳米金属氧化物的颗粒；例如，单一的絮状氢氧化Zr中间产物，其通过热处理得到晶态ZrO 2时，晶态ZrO 2往往烧结成极为致密的块状大颗粒，其内部少有缩松，因此难以通过后续砂磨、球磨过程将其破碎获得更细的晶态ZrO 2；而当絮状氢氧化Zr中间产物中复合有含Ti与含Nb的其它组分时，其不仅提高了其完全晶化的温度，还可以通过热处理得到疏松的、比表面积高的复合纳米金属氧化物颗粒，其主要由晶态ZrO 2组成并复合有含Ti与含Nb组分，该结构的颗粒可以很容易通过后续砂磨、球磨获得更细的复合纳米金属氧化物颗粒，见实施例1与对比实施例2。
进一步地，所述纳米钛酸薄膜经热处理后有演变成片状晶态纳米TiO 2的趋势；
进一步地，所述晶态纳米TiO 2片的厚度为2nm～20nm；所述晶态纳米TiO 2片的平均面积大于100nm 2；
进一步地，所述复合纳米金属氧化物中片状晶态纳米TiO 2的相组成包括板钛矿型TiO 2、纳米锐钛矿型纳米TiO 2、金红石型纳米TiO 2中的至少一种。
进一步地，所述絮状纳米氢氧化D经热处理后有演变成颗粒状晶态纳米DO 2的趋势；
进一步地，所述晶态纳米DO 2的粒径大小为3nm～500nm；
进一步地，所述纳米氧化M经热处理后有演变成晶态纳米氧化M的趋势；其形状包括薄膜状、颗粒状、板片状、条状、管棒状、烧结团聚状中的至少一种；
进一步地，所述晶态纳米氧化物M的形状为薄膜状时，其厚度为2nm～20nm；进一步优选为3nm～10nm；其薄膜的平均面积大于200nm 2；
进一步地，所述晶态纳米氧化物M的形状为颗粒状时，其粒径范围为3nm～500nm；
进一步地，所述晶态纳米氧化物M的形状为板片状时，其厚度为6nm～75nm，其板片的平均面积大于30nm 2；
进一步地，所述晶态纳米氧化物M的形状为长条状时，其直径范围为3nm～60nm，且长径比大于4；
进一步地，所述晶态纳米氧化物M的形状为管棒状时，其包括管状、棒状，其直径范围为3nm～200nm，且其长径比大于2；
进一步地，所述晶态纳米氧化M的形状为烧结团聚状时，其粒度因烧结团聚发生明显增大，粒径范围为5nm～1mm；
说明：上述所述各子类中间产物的特征，均是相应的A类元素(Ti元素、M类子元素、D类子元素)中各类子元素摩尔百分含量占主导地位时显示的特征与趋势；当某一类子元素摩尔百分含量不占主导地位时，由于各子类元素对应的各中间产物在形成过程中的相互影响，其可能不表现出其占主导地位时的演化与形成趋势。
特别地，当上述这种各子类元素不占主导的情况出现时，恰好体现了本申请其一方面各个步骤，以及后续其它几个方面制备复合纳米金属氧化物的巨大优势：因为复合纳米金属氧化物的性能的关键在于最终制备产物的性能，当各子类元素在析氢脱T过程中产生极大的交互作用并改变各自占主导时的演化形成趋势，就可以获得别的方法不可能获得的均匀复合；这种均匀复合的状态在其一方面步骤二出现后，会在其一方面步骤三与步骤四所对应过程中一直存在；且这种均匀复合不仅体现在物理混合均匀方面，还可体现在化学均匀复合方面，如生成全新的单相复合物质，其可以同时包括两到三个子类元素并以原子态均匀分布，如单相纳米氧化Ti/M；这种特殊的复合，可以使得最后获得的复合纳米金属氧化物获得极为优异的性能。
进一步地，所述晶化程度提高的复合纳米金属氧化物中，包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；且所述复合纳米金属氧化物中，Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相(细小的相的简称)的尺度进行异类元素对应氧化物的复合；其中，所述原子/原子团簇尺度大小为0.25nm-2.5nm；所述细相的平均粒径低于250nm；
进一步地，所述复合纳米金属氧化物中，Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相的尺度进行异类元素对应氧化物的原位嵌生复合。
说明：所述“异类元素对应的氧化物”，是指复合纳米金属氧化物中存在Ti元素、M类子元素、D类子元素这三类子元素中至少两类子元素时，所形成的复合纳米金属氧化物中，可以认为存在纳米氧化Ti、纳米氧化M、纳米氧化D中的至少两种。但是，由于异类元素氧化物复合可能产生的化学交互作用，实际在复合纳米金属氧化物中可能找不到纳米氧化Ti相，纳米氧化M相，或纳米氧化D相。因为某一类子类元素可能固溶在其它类子元素的氧化物中，或者异类子元素复合成为了一种新的多组元氧化物。例如，Ti固溶在氧化Zr中，该复合纳米金属氧化物只表现氧化Zr的晶体结构，则本申请仍然认为该复合纳米金属氧化物为氧化Ti与氧化Zr的复合。或者复合纳米金属氧化物是单相的氧化Ti/Nb，其不表现氧化Ti的晶体结构，也不表现出氧化Nb的晶体结构，而是表现一种新的晶体结构，则本申请也认为该复合纳米金属氧化物为氧化Ti与氧化Nb的复合。这两个例子中，Ti都没有以单独的氧化Ti相存在，所以Ti均是在原子/原子团簇尺度对异类元素对应氧化物进行复合的情形。当这些情形出现时，恰好实现了本申请制备的复合纳米金属氧化物的特殊复合，具有积极意义。(该解释适用于本申请所有方面，包括其一至其四方面相似情形)
其二方面，一种复合纳米金属氧化物中间产物的制备方法，其特征在于，包括如下步骤：
步骤1，过程与其一方面步骤一所述过程完全一致，具体见其一方面所述；
步骤2，过程与其一方面步骤二所述过程完全一致，具体见其一方面所述；
步骤3，过程与其一方面步骤三所述过程完全一致，具体见其一方面所述；
其二方面步骤1至步骤3与其一方面的步骤一至步骤三完全一致，包括各分步骤具体的详细说明部分，详情见其一方面的步骤一至步骤三所述，此处不在赘述。
其三方面，一种复合纳米金属氧化物的制备方法，其特征在于，包括如下步骤：
步骤(1)，提供初始合金，所述初始合金的成分组成包含T类元素与A类元素，其中T类元素包含Al、Zn中的至少一种；A类元素包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；其中，M类子元素包含Cr、V、Nb、Ta、W、Mo、Mn、Y、La、Ce、Pr、Nd、Pm、Sm、Eu、Gd、Tb、Dy、Ho、Er、Tm、Yb、Lu中的至少一种；D类子元素包含Zr、Hf中的至少一种；所述初始合金的成分组成主要为A xT y，其中x，y为对应各类元素的原子百分比含量，且5≤x≤55％，45％≤y≤95％；所述初始合金的凝固组织主要由A-T金属间化合物组成；
步骤(2)，将所述初始合金与温度为T 1，浓度为C 1的碱溶液混合；其中，T s溶液<T 1≤T f溶液，T f溶液为常压下所述参与反应的碱溶液的沸点温度；T s溶液为常压下所述参与反应的碱溶液的凝固点温度；
步骤(3)，将步骤(2)所得的固态物质与浓度为C 2的碱溶液混合，然后将混合物置于密闭容器中，然后在高于常压的T 2温度处理一段时间，其中，T 2>T f溶液；
步骤(4)，降温降压后，
当初始合金中不含D类子元素时，收集反应体系内的固态物质，即得到含M与Ti的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；且所述含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；其中，含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含M中间产物与含Ti中间产物两者之间至少有一个是相；
当初始合金中含D类子元素时，将液体加入降温降压后的反应体系中，使得稀释后的碱溶液浓度C 3<3mol/L，收集所有固态物质，即得到由含D固态物质与含M或(与)Ti的固态物质组成的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；其中，C 3<C 2；且当所述复合纳米金属氧化物中间产物中同时包括含M中间产物与含Ti中间产物时，含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；其中，含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含M中间产物与含Ti中间产物两者之间至少有一个是相；
步骤(5)，将步骤(4)所述复合纳米金属氧化物中间产物进行热处理，即得到晶化程度提高的复合纳米金属氧化物；其包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；且Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相的尺度进行异类元素对应氧化物的复合。
其三方面步骤(1)与其一方面的步骤一完全一致，包括具体的详细说明部分，详情见其一方面的步骤一所述，此处不在赘述；
所述步骤(2)中，
所述碱溶液包含NaOH、KOH、LiOH、RbOH、CsOH、Ba(OH) 2、Ca(OH) 2、Sr(OH) 2溶液中的至少一种；
进一步地，所述碱溶液中的溶剂包含水；作为优选，所述碱溶液中的溶剂为水；
进一步地，所述碱溶液中碱的浓度C 1为0.5mol/L～30mol/L；进一步地，所述碱溶液中碱的浓度C 1为1mol/L～30mol/L；作为优选，所述碱溶液中碱的浓度C 1为5mol/L～15mol/L；由于后续步骤(3)包含高温高压的反应，因此碱溶液浓度C 1范围的低值可以低至0.5mol/L。在此浓度下，结合高温高压条件，也能实现相应的目标反应。
进一步地，所述与初始合金混合的碱溶液中的碱为过量剂量，碱的摩尔数为初始合金摩尔数的5倍以上；进一步地，碱的摩尔数为初始合金摩尔数的10倍以上；进一步地，碱的摩尔数为初始合金摩尔数的20倍以上；
可以理解，将所述初始合金与温度为T 1，浓度为C 1的碱溶液混合的同时将会发生析氢脱T反应；且碱溶液温度越高，碱溶液浓度越高，反应速率越快。
当所述初始合金与温度为T 1，浓度为C 1的碱溶液混合，析氢脱T反应过程中反应界面以不低于2μm/min的平均速率由初始合金表面向内推进时，其即为其一方面步骤二所述情况，详情见其一方面步骤二所示。在此情况下，反应过程中初始合金通过析氢脱T反应发生纳米碎化，并经形状与成分重构生成纳米尺度的含M固态产物；因此，所述步骤(2)包含了其一方面步骤二所述情况，即在其一方面步骤二所述情况之后，进行后续步骤(3)处理，仍然属于本申请其三方面保护的范畴。
当存在后续步骤(3)的情况下，所述步骤(2)不论发生纳米碎化与否，或者步骤(2)所述初始合金与碱溶液混合后析氢脱T反应完毕与否，都不对步骤(3)的反应的结果产生根本性的影响。因为步骤(3)的反应在更长的时间， 更高的温度，尤其更高的压力下进行，无论步骤(2)中温度T 1与浓度C 1的值如何，或者无论步骤(2)所得中间产物如何，其反应物或中间产物的特征都会被后续过程所覆盖，并在步骤(3)达到新的反应平衡，同时获得该平衡条件下的最终产物。
因此，所述步骤(2)中，当所述初始合金与温度为T 1，浓度为C 1的碱溶液混合，析氢脱T反应过程中反应界面以低于2μm/min的平均速率由初始合金表面向内推进时，仍然属于本申请其三方面保护的范畴。
进一步地，T s溶液≤T 1<60℃；进一步地，T s溶液≤T 1<80℃；
所述步骤(3)中，
将步骤(2)所得固态物质与浓度为C 2的碱溶液混合，然后将混合物置于密闭容器中的过程，具体操作过程包括如下两种方案中的至少一种：
a)直接将步骤(2)所得固态物质与浓度为C 1的碱溶液混合物置于密闭容器中；此时，不需要增减碱溶液，且C 2≈C 1，C 2与C 1的浓度微小差别来源于步骤(2)中因析氢脱T反应导致的少量碱的消耗；
b)先将步骤(2)所得固态物质与浓度为C 1的碱溶液分离，再与浓度为C 2的碱溶液混合并置于密闭容器中；此时，浓度为C 2的碱溶液与浓度为C 1的碱溶液的浓度及碱品种可以一致，也可以与浓度为C 1的碱溶液的浓度及碱品种不一致；
进一步地，所述C 2的范围为0.5mol/L～30mol/L；进一步地，所述C 2的范围为1mol/L～30mol/L；进一步地，所述C 2的范围为5mol/L～30mol/L；
进一步地，所述压力高于常压，但低于100MPa；进一步地，所述压力高于常压，但低于20MPa；
进一步地，T f溶液<T 2≤500℃；进一步地，T f溶液<T 2≤300℃；
进一步地，所述在高于常压的T 2温度处理时间为1mim～48h；进一步地，所述在高于常压的T 2温度处理时间为1mim～12h；进一步地，所述在高于常压的T 2温度处理时间为1mim～2h；进一步地，所述在高于常压的T 2温度处理时间为1mim～30mim；进一步地，所述在高于常压的T 2温度处理时间为1mim～10min；
进一步地，所述在高于常压的T 2温度的处理时间与C 2的浓度，压力大小，以及T 2的大小相关；C 2的浓度越高，压力越大，T 2越高，则所需反应时间越短。当C 2的浓度取其范围低值，如0.5mol/L，且溶剂为水时，即为水热反应常用条件，低浓度碱即为水热反应条件下的矿化剂；
进一步地，当C 2的范围为7mol/L～30mol/L时，所述在高于常压的T 2温度处理时间为1mim～2h；
进一步地，当C 2的范围为7mol/L～30mol/L时，所述在高于常压的T 2温度处理时间为1mim～30mim；
进一步地，当C 2的范围为0.5mol/L～7mol/L时，所述在高于常压的T 2温度处理时间为30mim～48h；
所述步骤(4)中，
进一步地，所述降温，为降温至100℃以下；进一步地，所述降温，为降温至50℃以下；
当初始合金中不含D类子元素时，收集反应体系内的固态物质，即得到含M与Ti的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；且所述含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；其中，含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含M中间产物与含Ti中间产物两者之间至少有一个是相；
进一步地，含Ti中间产物为相时，含Ti中间产物的形状包括薄膜状、管状、棒状、纤维状中的至少一种；
进一步地，含Ti中间产物为相时，含Ti中间产物的形状包括管状、棒状、纤维状中的至少一种；
进一步地，收集所述反应体系内固态物质的过程，包括对含M与Ti的复合纳米金属氧化物中间产物的分离收集，清洗，干燥过程；
进一步地，所述清洗过程包括通过稀酸溶液对含M与Ti的复合纳米金属氧化物中间产物清洗至PH＝4-8，清洗的作用包括清除所述含M与Ti的复合纳米金属氧化物中间产物上残留的碱，同时对纳米钛酸盐进行阳离子调整。
作为优选，所述稀酸溶液中氢离子浓度为0.001mol/L～0.1mol/L；
进一步地，所述含M中间产物主要为纳米氧化M；
进一步地，所述含Ti中间产物主要为纳米钛酸盐；
进一步地，当对含M与Ti的复合纳米金属氧化物中间产物进行稀酸清洗后，含M与Ti的复合纳米金属氧 化物中间产物中的纳米钛酸盐转变为纳米钛酸，即纳米钛酸盐发生H +与钛酸盐阳离子的置换。进一步地，所述纳米钛酸盐的形状包括薄膜状、管状、棒状、纤维状中的至少一种；
进一步地，酸洗后，所述含Ti中间产物主要为纳米钛酸；
进一步地，所述含M与Ti的复合纳米金属氧化物中间产物的组成包含纳米氧化M，同时包含纳米钛酸盐与纳米钛酸中的至少一种；
进一步地，所述纳米钛酸盐的形状包括管状、棒状、纤维状中的至少一种；且其横截面直径为2nm-20nm；
进一步地，所述纳米钛酸的形状包括管状、棒状、纤维状中的至少一种；且其横截面直径为2nm-20nm；
进一步地，所述含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；原位嵌生复合的特征及解释其一方面已有描述，见其一方面；此处与其一方面所述唯一不同点是：其一方面所述含Ti中间产物主要为薄膜状，而此处所述含Ti中间产物的形状包括薄膜状、管状、棒状、纤维状中的至少一种；
进一步地，所述含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；
进一步地，所述含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合，且当含M中间产物与含Ti中间产物组合成某种接近单一的结构，如含M/Ti的中间产物时，其也属于这种原位嵌生复合的情形。此时，含M中间产物与含Ti中间产物均是具有某种结构的含M/Ti的中间产物，且其中M与Ti在原子尺度原位嵌生复合，为最彻底的复合。
进一步地，所述纳米氧化M与纳米钛酸盐复合的方式包括原位嵌生复合；
进一步地，所述纳米氧化M与纳米钛酸复合的方式包括原位嵌生复合；
进一步地，纳米氧化M包括低结晶度的纳米氧化M、晶态纳米氧化M、水合纳米氧化M中的至少一种；
进一步地，所述低结晶度纳米氧化M包括非晶态的纳米氧化M；
由于纳米氢氧化M可以看做是纳米氧化M与H 2O的结合体，通过较低的温度进行加热脱水即可得到纳米氧化M，因此所述水合纳米氧化M即为纳米氢氧化M；
进一步地，所述纳米氧化M具有颗粒分散性；
进一步地，所述纳米氧化M中不同价态的M对应于不同的纳米氧化M；如氧化Mn可以为MnO，也可以为MnO 2；
进一步地，所述纳米氧化M的形状在三维方向上至少有一维的尺度不超过500nm；
进一步地，所述纳米氧化M的形状在三维方向上至少有一维的尺度不超过250nm；
进一步地，所述纳米氧化M的形状在三维方向上至少有一维的尺度不超过150nm；
进一步地，所述纳米氧化M的形状包括薄膜状、颗粒状、板片状、条状、管棒状、团絮状中的至少一种；所述团絮状是指极其细小且没有明显棱角的微结构团聚在一起的状态。
进一步地，所述纳米氧化M虽然可以软团聚在一起，但其不通过三维连续刚性网络状结构紧密连接在一起，并维持原初始合金的外形。
进一步地，所述纳米氧化M主要为薄膜状时，其厚度为0.25nm～30nm；且薄膜的平均面积大于100nm 2；
进一步地，所述纳米氧化M主要为颗粒状时，其粒径范围为1.5nm～500nm；优选为1.5nm～200nm；优选为1.5nm～100nm；
进一步地，所述纳米氧化M主要为板片状时，其厚度范围为1.5nm～100nm，优选为5nm～30nm，进一步优选为5nm～20nm；且板片的平均面积大于100nm 2；
进一步地，所述纳米氧化M主要为团絮状时，其团絮微结构的大小为1nm～15nm；
进一步地，所述纳米氧化M主要为管棒状时，其包括管状、棒状，其直径范围为2nm～200nm；进一步优选为2nm～50nm；且其长径比大于2；
当初始合金中含D类子元素时，将液体加入降温降压后的反应体系中，使得稀释后的碱溶液浓度C 3<3mol/L，收集所有固态物质，即得到由含D固态物质与含M或(与)Ti的固态物质组成的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；其中，C 3<C 2，且当所述复合纳米金属氧化物中间产物中同时包括含M中间产物与含Ti中间产物时，含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；其中，含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含M中间产物与含Ti中间产物两者之间至少有一个是相。
进一步地，由于含M或(与)Ti的固态物质形成的同时，也必然有少部分D类子元素被限制在其中，从而在先形成的含M或(与)Ti的固态物质中也有少量D类子元素参与的复合；
进一步地，含Ti中间产物为相时，含Ti中间产物的形状包括薄膜状、管状、棒状、纤维状中的至少一种；
进一步地，所述液体包含水；
进一步的，所述液体的温度为常温；进一步的，所述液体的温度为0℃～40℃；
进一步地，C 3<3mol/L；进一步地，C 3<2mol/L，
即碱溶液的浓度降低到C 3以下，当稀释之前D类子元素已经溶解在C 2碱溶液中时，通过调整C 3的浓度值，可以使D类元素在稀释后的碱溶液中以絮状氢氧化D的方式析出；当稀释之前D类元素没有溶解且已经是固态时，此时则不发生氢氧化D的析出。
进一步地，稀释之前，C 2处于其范围高值区域，如7-30mol/L时，D类元素溶于碱溶液中；稀释之后，D类元素在稀释后的碱溶液中以絮状氢氧化D的方式析出；进一步地，所述纳米氢氧化D主要为低结晶度的纳米氢氧化D；进一步地，所述纳米氢氧化D为絮状结构，其絮状微结构的尺寸范围为0.5nm～10nm；
进一步地，稀释之前，C 2处于其范围低值区域，如0.5-3mol/L时，稀释之前D类元素已经通过高温高压水热反应变成固态纳米DO 2，其中，较低浓度碱的作用为矿化剂；则稀释之后，仍然保留固态纳米DO 2；
进一步地，所述纳米DO 2的粒径大小为3nm～500nm；
进一步地，稀释之前，C 2处于其范围中值区域，如3-7mol/L时，D类元素的演化规律介于上述两者之间；即稀释之后，获得含D产物包括固态纳米DO 2与絮状氢氧化D；
进一步地，所述稀释的用液体中含有表面活性剂或修饰剂；
液体中添加表面活性剂或修饰剂的目的在于：控制析出的纳米氧化D的颗粒大小，抑制其异常合并长大；进一步地，所述表面活性剂或修饰剂包括PVP、CTAB、CTAC中的至少一种；
进一步地，收集所述所有固态物质的过程，包括对所述所有固态物质的分离收集，清洗，干燥过程；
进一步地，所述清洗过程包括通过稀酸溶液对所有固态物质清洗至PH＝4-8，清洗的作用包括清除所述所有固态物质上残留的碱，同时对存在的纳米钛酸盐进行阳离子调整。
进一步地，当对含Ti的固态物质进行稀酸清洗后，含Ti的固态物质中的纳米钛酸盐转变为纳米钛酸，即纳米钛酸盐发生H +与钛酸盐阳离子的置换。
作为优选，所述稀酸溶液中氢离子浓度为0.0001mol/L～0.09mol/L；
进一步地，所述含M中间产物主要为纳米氧化M；
进一步地，所述含Ti中间产物主要为纳米钛酸盐；
进一步地，当对含M与Ti的复合纳米金属氧化物中间产物进行稀酸清洗后，含M与Ti的复合纳米金属氧化物中间产物中的纳米钛酸盐转变为纳米钛酸，即纳米钛酸盐发生H +与钛酸盐阳离子的置换。进一步地，所述纳米钛酸盐的形状包括薄膜状、管状、棒状、纤维状中的至少一种；其中，C 2浓度越高，纳米钛酸盐越易形成管状、棒状、纤维状；
进一步地，酸洗后，所述含Ti中间产物主要为纳米钛酸；
进一步地，所述含M与Ti的复合纳米金属氧化物中间产物的组成包含纳米氧化M，同时包含纳米钛酸盐与纳米钛酸中的至少一种；
进一步地，所述纳米钛酸盐的形状包括薄膜状、管状、棒状、纤维状中的至少一种；且薄膜厚度为0.5nm-10nm；管状、棒状、纤维状的横截面直径为2nm-20nm；
进一步地，所述纳米钛酸的形状包括薄膜状、管状、棒状、纤维状中的至少一种；且薄膜厚度为0.5nm-10nm；管状、棒状、纤维状的横截面直径为2nm-20nm；
进一步地，所述含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；原位嵌生复合的特征及解释其一方面已有描述，见其一方面；此处与其一方面所述唯一不同点是：其一方面所述含Ti中间产物主要为薄膜状，而此处所述含Ti中间产物的形状包括薄膜状、管状、棒状、纤维状中的至少一种；
进一步地，所述纳米氧化M与纳米钛酸盐复合的方式包括原位嵌生复合；
进一步地，所述纳米氧化M与纳米钛酸复合的方式包括原位嵌生复合；
进一步地，纳米氧化M包括低结晶度的纳米氧化M、晶态纳米氧化M、水合纳米氧化M中的至少一种；
进一步地，所述低结晶度纳米氧化M包括非晶态的纳米氧化M；
由于纳米氢氧化M可以看做是纳米氧化M与H 2O的结合体，通过较低的温度进行加热脱水即可得到纳米氧化M，因此所述水合纳米氧化M即为纳米氢氧化M；
进一步地，所述纳米氧化M具有颗粒分散性；
进一步地，所述纳米氧化M中不同价态的M对应于不同的纳米氧化M；如氧化Mn可以为MnO，也可以为MnO 2；
进一步地，所述纳米氧化M的形状在三维方向上至少有一维的尺度不超过500nm；
进一步地，所述纳米氧化M的形状在三维方向上至少有一维的尺度不超过250nm；
进一步地，所述纳米氧化M的形状在三维方向上至少有一维的尺度不超过150nm；
进一步地，所述纳米氧化M的形状包括薄膜状、颗粒状、板片状、条状、管棒状、团絮状中的至少一种；所述团絮状是指极其细小且没有明显棱角的微结构团聚在一起的状态。
进一步地，所述纳米氧化M虽然可以软团聚在一起，但其不通过三维连续刚性网络状结构紧密连接在一起，并维持原初始合金的外形。
进一步地，所述纳米氧化M主要为薄膜状时，其厚度为0.25nm～30nm；且薄膜的平均面积大于100nm 2；
进一步地，所述纳米氧化M主要为颗粒状时，其粒径范围为1.5nm～500nm；优选为1.5nm～200nm；优选为1.5nm～100nm；
进一步地，所述纳米氧化M主要为板片状时，其厚度范围为1.5nm～100nm，优选为5nm～30nm，进一步优选为5nm～20nm；且板片的平均面积大于100nm 2；
进一步地，所述纳米氧化M主要为团絮状时，其团絮微结构的大小为1nm～15nm；
进一步地，所述纳米氧化M主要为管棒状时，其包括管状、棒状，其直径范围为2nm～200nm；进一步优选为2nm～50nm；且其长径比大于2；
需要说明的是：所述步骤(4)中，所涉及的纳米氧化M、纳米钛酸盐、纳米氢氧化D或DO 2的形貌特征，均是相应组分体积占主导地位时显示的特征；当某一中间产物组分体积不占主导地位时，由于各个中间产物组分之间的相互影响，其可能不显示其体积占主导地位时的形貌特征。例如，纳米钛酸盐这一中间产物组分，当其与纳米氧化Nb复合，且其体积百分比超过50％时，其可以显现管状状态，但当其体积百分比低于20％时，受纳米氧化Nb的影响(如被嵌生在其中)，则其可能不显示出管状的状态。
进一步地，所述复合纳米金属氧化物中间产物的热稳定性或(与)晶化温度高于相似工艺制备的对应的单一纳米金属氧化物中间产物的热稳定性或(与)晶化温度。这种热稳定性或(与)晶化温度的提高，与不同的A类子元素(元素Ti、M类子元素、D类子元素)在复合纳米金属氧化物中间产物中的特殊复合有关。这种提高热稳定性或(与)晶化温度的复合包括两类：一类是初始原位嵌生复合，包括原子、原子团簇、相尺度的原位嵌生；另一类是超细、超高分散性絮状氢氧化D参与的物理吸附复合，其在后期热处理过程中会诱导烧结嵌生复合。
进一步地，所述复合纳米金属氧化物中间产物中，包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；且所述复合纳米金属氧化物中间产物中，Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相(细小的相的简称)的尺度进行异类元素对应氧化物中间产物的复合；其中，所述原子/原子团簇尺度大小为0.25nm-2.5nm；所述细相的平均粒径低于250nm；
进一步地，所述复合纳米金属氧化物中间产物中，Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相的尺度进行异类元素对应氧化物中间产物的原位嵌生复合。
所述步骤(5)中，
进一步地，所述热处理的温度为300℃～2000℃；进一步地，所述热处理的温度为400℃～2000℃；进一步地，所述热处理的温度为500℃～2000℃；
进一步地，所述热处理时间为1min～24h；进一步地，所述热处理时间为5min～24h；
进一步地，所述热处理时间为30min～24h；
可以理解，随着热处理时间的延长，热处理温度的升高，所得热处理产物的结晶度不断提高，直到全部晶化。
进一步地，所述晶化程度提高的复合纳米金属氧化物中，Ti元素、M类子元素、D类子元素这三类元素在原子/原子团簇尺度或细相(细小的相的简称)的尺度进行异类元素的复合；其中，所述原子/原子团簇尺度大小为0.25nm-2.5nm；所述细相的平均粒径低于250nm；
进一步地，所述Ti元素对应的相为部分晶化或全部晶化的纳米TiO 2；所述M类子元素对应的相为部分晶化或全部晶化的纳米氧化M、所述D类子元素对应的相为部分晶化或全部晶化的纳米DO 2；
进一步地，所述细相的平均粒径低于125nm；进一步地，所述细相的平均粒径低于50nm；
进一步地，所述细相的平均粒径低于25nm；进一步地，所述细相的平均粒径低于15nm；
所述原子/原子团簇尺度为0.25nm-2.5nm；其中原子尺度为0.25nm-0.5nm，原子团簇尺度为0.5nm-2.5nm；在0.25nm-2.5nm尺度，不足以形成一个相，只能称之为原子或原子团簇；
作为优选，所述晶化程度提高的复合纳米金属氧化物中，Ti元素、M类子元素、D类子元素这三类元素在原子/原子团簇尺度进行异类元素的复合；其中，所述原子/原子团簇尺度大小为0.25nm-2.5nm。
进一步地，各A类元素子类元素所对应的相的晶化程度与热处理温度和时间相关；根据相转化规律，部分晶化的纳米TiO 2可能含有钛酸的组分；部分晶化的纳米氧化M可能含有氢氧化M组分；部分晶化的纳米DO 2可能含有氢氧化D的组分。
关于“所述晶化程度提高的复合纳米金属氧化物中，Ti元素、M类子元素、D类子元素这三类元素在原子/原子团簇尺度或细相的尺度进行异类元素的复合；其中，所述原子/原子团簇尺度大小为0.25nm-2.5nm；所述细相的平均粒径低于250nm”的理解：即晶化程度提高的复合纳米金属氧化物中，把Ti元素、M类子元素、D类子元素各自对应的组分单独分开来评判，其尺度较小的组分的粒度要么是原子/原子团簇级别(0.25nm-2.5nm)，要么是平均粒径低于250nm的细相级别。举例来说：如果晶化程度提高的复合纳米金属氧化物为(TiCr)O 2，其为少量Cr以原子或原子团簇嵌入TiO 2形成，则Ti元素、Cr元素(属于M类子元素)在原子/原子团簇尺度进行了异类元素的复合；如果晶化程度提高的复合纳米金属氧化物为ZrO 2相为与氧化Cr相的复合时，则两者中尺度较小的相其平均粒径为低于250nm且大于2.5nm的细相级别，即细相的表述为出现两个或两个以上相的情形，且细相为平均尺度较小的那个相。
进一步地，所述晶化程度提高的复合纳米金属氧化物中，Ti元素、M类子元素、D类子元素这三类元素在细相的尺度进行异类元素的复合时，复合纳米金属氧化物在热处理过程中的演化规律及产物特征包括如下特征：
当初始合金中不含D类子元素时，所述复合纳米金属氧化物主要为纳米氧化M与纳米TiO 2的复合；且所述纳米氧化M与纳米TiO 2复合的方式包括原位嵌生复合；
当初始合金中含D类子元素时，所述复合纳米金属氧化物主要为纳米DO 2与纳米氧化M或(与)纳米TiO 2的复合；且当所述复合纳米金属氧化物中同时包括纳米氧化M与纳米TiO 2时，纳米氧化M与纳米TiO 2复合的方式包括原位嵌生复合。
进一步地，所述复合纳米金属氧化物中间产物在进行热处理之前稀酸清洗至PH＝4-8，以清除复合纳米金属氧化物中间产物上的残余碱；同时，当复合纳米金属氧化物中间产物中含有纳米钛酸盐时，稀酸清洗可将纳米钛酸盐转变为纳米钛酸；
进一步地，所述纳米DO 2与纳米氧化M或(与)纳米TiO 2的复合，包括三种情况：纳米DO 2与纳米氧化M的复合；纳米DO 2与纳米TiO 2的复合；纳米DO 2与纳米氧化M，及纳米TiO 2的复合；
a)进一步地，所述热处理过程中，随着热处理温度提高，热处理时间提高，所述复合纳米金属氧化物中间产物中的纳米钛酸逐步向锐钛矿型TiO 2转变，然后进一步向金红石型TiO 2转变；
b)进一步地，所述热处理过程中，随着热处理温度提高，热处理时间提高，所述复合纳米金属氧化物中间产物中的纳米氢氧化D逐步向晶态纳米DO 2转变；其中，所述晶态DO 2包括三种情况中的至少一种：ZrO 2，HfO 2，(Zr/Hf)O 2；
c)进一步地，所述热处理过程中，随着热处理温度提高，热处理时间提高，所述复合纳米金属氧化物中间产物中的纳米氧化M逐步向晶态纳米氧化M转变；
可以理解，随着热处理时间的延长，热处理温度的升高，所得热处理产物的结晶度不断提高，直到全部晶化。因此，上述a)-c)三种情况复合纳米金属氧化物中间产物的转变程度与热处理时间和温度相关。在一定的热 处理时间和温度条件下，任何结晶程度(结晶度为0-100％)的产物均是本申请所保护的范围；只要热处理时间足够长，温度足够高，复合纳米金属氧化物中间产物均能完全发生上述a)-c)的转变。
因此，当复合纳米金属氧化物中间产物原来就是原位嵌生状态，如纳米氧化M与纳米钛酸的原位嵌生复合，其在烧结之前即处于最佳均匀分散状态，则烧结后仍然可以获得最佳的均匀分散状态；
进一步地，所述复合纳米金属氧化物的颗粒疏松性或(与)比表面积高于相似工艺制备的对应的单一纳米金属氧化物的的颗粒疏松性或(与)比表面积。该现象产生的原因与上述复合纳米金属氧化物中间产物热稳定性或(与)晶化温度提高的原因类似，均与初始原位嵌生复合或热处理诱导的烧结嵌生复合相关。例如，热处理之后，由Zr与Ti元素组成的复合纳米金属氧化物的颗粒疏松性或(与)比表面积高于单独由Zr或单独由Ti元素组成的纳米金属氧化物的颗粒疏松性或(与)比表面积。
当所述晶化程度提高的复合纳米金属氧化物的颗粒疏松性或比表面积提高后，其更容易通过后续砂磨、球磨获得更细的晶化程度提高的复合纳米金属氧化物的颗粒。
进一步地，所述复合纳米金属氧化物中片状晶态纳米TiO 2的相组成包括板钛矿型TiO 2、纳米锐钛矿型纳米TiO 2、金红石型纳米TiO 2中的至少一种；其直径为3nm～500nm；
进一步地，所述晶态纳米DO 2的粒径大小为3nm～500nm；
进一步地，所述纳米氧化M经热处理后有演变成晶态纳米氧化M的趋势；其形状包括薄膜状、颗粒状、板片状、条状、管棒状、烧结团聚状中的至少一种；
进一步地，所述纳米氧化M中不同价态的M对应于不同的纳米氧化M；如氧化Mn可以为MnO，也可以为MnO 2；
进一步地，所述晶态纳米氧化物M的形状为薄膜状时，其厚度为2nm～20nm；进一步优选为3nm～10nm；其薄膜的平均面积大于200nm 2；
进一步地，所述晶态纳米氧化物M的形状为颗粒状时，其粒径范围为3nm～500nm；
进一步地，所述晶态纳米氧化物M的形状为板片状时，其厚度为6nm～75nm，其板片的平均面积大于30nm 2；
进一步地，所述晶态纳米氧化物M的形状为长条状时，其直径范围为3nm～60nm，且长径比大于4；
进一步地，所述晶态纳米氧化物M的形状为管棒状时，其包括管状、棒状，其直径范围为3nm～200nm，且其长径比大于2；
进一步地，所述晶态纳米氧化M的形状为烧结团聚状时，其粒度因烧结团聚发生明显增大，粒径范围为5nm～1mm。
进一步地，所述晶化程度提高的复合纳米金属氧化物中，包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；且所述复合纳米金属氧化物中，Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相(细小的相的简称)的尺度进行异类元素对应氧化物的复合；其中，所述原子/原子团簇尺度大小为0.25nm-2.5nm；所述细相的平均粒径低于250nm；
进一步地，所述复合纳米金属氧化物中，Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相的尺度进行异类元素对应氧化物的原位嵌生复合。
其四方面，一种复合纳米金属氧化物中间产物的制备方法，其特征在于，包括如下步骤：
步骤1)，过程与其三方面步骤(1)所述过程完全一致，具体见其三方面所述；
步骤2)，过程与其三方面步骤(2)所述过程完全一致，具体见其三方面所述；
步骤3)，过程与其三方面步骤(3)所述过程完全一致，具体见其三方面所述；
步骤4)，过程与其三方面步骤(4)所述过程完全一致，具体见其三方面所述；
所述步骤4)中，
进一步地，所述含Ti中间产物为相时，其形状包括薄膜状、管状、棒状、纤维状中的至少一种。
进一步地，所述含Ti中间产物为相时，其形状包括管状、棒状、纤维状中的至少一种。
其四方面步骤1)至步骤4)与其三方面的步骤(1)至步骤(4)完全一致，包括各分步骤具体的详细说明部分，详情见其三方面的步骤(1)至步骤(4)所述，此处不在赘述。
其五方面，本申请还涉及一种复合纳米金属氧化物，其特征在于，根据其一方面所述制备方法制备，其制 备过程及详细特征见其一方面步骤一至步骤四所述，其详细特征还包括：
所述复合纳米金属氧化物中，包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；且所述复合纳米金属氧化物中，Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相(细小的相的简称)的尺度进行异类元素对应氧化物的复合；其中，所述原子/原子团簇尺度大小为0.25nm-2.5nm；所述细相的平均粒径低于250nm；其中，M类子元素包含Cr、V、Nb、Ta、W、Mo、Mn、Y、La、Ce、Pr、Nd、Pm、Sm、Eu、Gd、Tb、Dy、Ho、Er、Tm、Yb、Lu中的至少一种；D类子元素包含Zr、Hf中的至少一种。
进一步地，所述复合纳米金属氧化物中，Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相的尺度进行异类元素对应氧化物的原位嵌生复合。
其六方面，本申请还涉及一种复合纳米金属氧化物中间产物，其特征在于，根据其二方面所述制备方法制备，其制备过程及详细特征见其二方面步骤一至步骤三所述，其详细特征还包括：
所述复合纳米金属氧化物中间产物中，包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；且所述复合纳米金属氧化物中间产物中，Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相(细小的相的简称)的尺度进行异类元素对应氧化物中间产物的复合；其中，所述原子/原子团簇尺度大小为0.25nm-2.5nm；所述细相的平均粒径低于250nm；
进一步地，所述复合纳米金属氧化物中间产物中，Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相的尺度进行异类元素对应氧化物中间产物的原位嵌生复合。
其七方面，本申请还涉及一种复合纳米金属氧化物，其特征在于，根据其三方面所述制备方法制备，其制备过程及详细特征见其三方面所述。
其八方面，本申请还涉及一种复合纳米金属氧化物中间产物，其特征在于，根据其四方面所述制备方法制备，其制备过程及详细特征见其四方面所述。
其九方面，本申请还涉及其一至其四方面任一方面所述制备方法制备的产物材料，或其五方面至其八方面所述材料，在复合材料、催化材料、陶瓷材料、耐火材料、先进电子材料、电池材料、变色材料、吸波材料、污水降解材料、杀菌材料、涂料、颜料、热喷涂材料、传感器中的应用。
其十方面，一种复合氧化物陶瓷的制备方法，其特征在于，包括如下步骤：
步骤S1，制备混合均匀且细化的混合粉料，所述混合粉料的组成包括其一方面至其四方面任一方面所述制备方法制备的复合纳米金属氧化物或中间产物，以及外加粉体；其中，所述复合纳米金属氧化物或中间产物在混合粉料中的摩尔百分比含量为V 1，外加粉体在混合粉料中的摩尔百分比含量为V 2，且所述外加粉体包含Al 2O 3、CaO、MgO、SiO 2、B 2O 3、BeO中的至少一种，1％≤V 1≤100％，0≤V 2≤99％；
步骤S2，将混合粉料压制成为坯体，经高温焙烧，即制得复合氧化物陶瓷材料。
所述步骤S1中，
进一步地，2％≤V 1≤100％；0≤V 2≤98％；进一步地，10％≤V 1≤100％；0≤V 2≤90％；进一步地，50％≤V 1≤100％；0≤V 2≤50％；
当V 2＝0时，不需要外加粉体；但可以通过混料过程将粉料进一步均匀混合，并同时细化；
当V 2>0时，混合粉料里面除了其一方面至其四方面任一方面所述制备方法制备的复合纳米金属氧化物或中间产物外，还含有外加粉体组分，因此需要通过混料过程将混合粉料均匀混合，并同时细化；
进一步地，所述制备混合均匀且细化的混合粉料的过程包括球磨、砂磨中的至少一种；当混料过程为湿法时，混料过程处理完毕后经烘干得到混合均匀且细化的混合粉料；在混料过程中，同时实现粉料的破碎及细化；
进一步地，所述其一方面至其四方面任一方面所述制备方法制备的复合纳米金属氧化物或中间产物中包含氢氧化D或(与)DO 2；
进一步地，所述其一方面至其四方面任一方面所述制备方法制备的复合纳米金属氧化物或中间产物中包含DO 2与氧化Y；
其一方面至其四方面任一方面所述制备方法制备的复合纳米金属氧化物或中间产物中ZrO 2的摩尔百分含量大于50％；
进一步地，所述混合粉料中ZrO 2的摩尔百分含量大于25％；进一步地，所述混合粉料中ZrO 2的摩尔百分含量大于50％；进一步地，所述混合粉料中ZrO 2的摩尔百分含量大于75％；
进一步地，所述混合粉料中ZrO 2的摩尔百分含量大于75％，且混合粉料中包括ZrO 2与Y 2O 3复合的复合纳米金属氧化物；
所述步骤S2中，
进一步地，所述压制坯体的成型压力为5MPa～800MPa；进一步地，所述压制坯体的成型压力5MPa～80MPa；
进一步地，所述焙烧温度为500℃～2000℃；进一步地，所述焙烧温度为500℃～1500℃；
进一步的，所述压制成为坯体，经高温焙烧的过程包括压制同时加温焙烧、先压制再焙烧两种方案中的至少一种。
其十一方面，一种复合氧化物陶瓷，其特征在于，根据其十方面所述制备方法制备，其详细特征见其十方面所述。
本发明的有益效果主要体现在以下几个方面：
首先，通过合金为原料，可以一次性制备多种组分的复合纳米金属氧化物。以氧化Nb(Nb 2O 5)、TiO 2、ZrO 2组成的复合纳米金属氧化物的制备来说，传统方法首先需要分别制备Nb 2O 5、TiO 2、ZrO 2三种纳米金属氧化物，然后再将其混合均匀，得到复合纳米金属氧化物。由于粉体材料的团聚问题，其很难保证其均匀混合，且所有的混合均是物理混合。进一步改进的方法，可以通过分别制备Nb-T金属间化合物初始合金、Ti-T金属间化合物初始合金、Zr-T金属间化合物初始合金，然后将三种金属间化合物合金混合再进行与本申请相似的析氢脱T反应过程。虽然这种方法有所改进，但存在两个弊端：需要制备三种金属间化合物初始合金；由于Nb、Ti在初始合金中分属不同的金属间化合物，其很难确保获得原位嵌生复合的含Nb中间产物与含Ti中间产物。而在本申请中，只需要根据最终复合纳米金属氧化物中A类元素Nb、Ti、Zr的摩尔比例，如摩尔比Nb：Ti：Zr＝1:1:1，选择Al为T，然后根据Al-Ti、Al-Nb、Al-Zr相图，选择合适的Al含量，确保A-T金属间化合物中，Nb、Ti、Zr元素均存在于金属间化合物Al-(Nb/Ti/Zr)中，且此时不需要关心Al-(Nb/Ti/Zr)金属间化合物具体有几个金属间化合物相，也不需要关心每个相的组成中是否含有Nb、Ti、Zr元素中的一种、两种、或者三种。如此操作，则通过一个初始合金即可以设计好复合纳米金属氧化物中Nb、Ti、Zr的摩尔比例。此外，由于Al-(Nb/Ti/Zr)金属间化合物中，各元素相互之间存在很大的固溶度，如TiAl 3金属间化合物中，原来25％的Ti，若其中5％的Ti被Nb替代时，Nb以固溶的方式存在其中时，则获得的Ti(Nb)Al 3金属间化合物仍然与TiAl 3金属间化合物拥有几乎相同的晶体结构。此时，Nb、Ti同时存在于一个金属间化合物中，析氢脱T反应过程中两者演化过程同时原位进行，这就为后续Nb 2O 5与TiO 2形成原位嵌生复合提供了可能。且产物同时生成，可以保证复合组分产物的均匀性。这些特征，都可以使得复合纳米金属氧化物获得更为优异的性能。
特别地，当A类元素各子类元素不占主导的情况出现时，恰好体现了本申请其一方面各个步骤，以及后续其它几个方面制备复合纳米金属氧化物的巨大优势：因为复合纳米金属氧化物的性能的关键在于最终制备产物的性能，当各子类元素之间在析氢脱T过程中产生极大的交互作用影响并改变各自占主导时的演化形成趋势，就可以获得别的方法不可能获得的均匀复合；这种均匀复合的状态在其一方面步骤二所述过程存在后，会在其一方面步骤三与步骤四所对应制备过程中一直存在；且这种均匀复合不仅体现在物理混合均匀方面，还可体现在化学均匀复合方面，如生成全新的单相复合物质，其同时包括两到三个子类元素并以原子或原子团簇的尺度均匀分布，如单相纳米氧化Ti/M；这种特殊的复合，可以使得最后获得的复合纳米金属氧化物获得极为优异的性能。
其次，实现了复合纳米金属氧化物的短时高效制备。虽然强碱水热法是目前较为成熟的制备诸如纳米钛酸盐、纳米钛酸及纳米TiO 2的工艺，但该反应需要采用高压反应容器，一般以纳米TiO 2和高浓度强碱(如NaOH溶液)为原料，在高温条件下进行极长时间的水热合成，反应得到钛酸盐(如钛酸钠)，经过中和酸洗后一般 得到钛酸纳米管。例如，2001年有文献报道，以工业锐钛矿型TiO 2和10mol/L氢氧化钠溶液为原料，在130℃条件下，与高压反应容器中水热反应72h后，得到管长为几十到几百纳米，内径为5.3nm的钛酸纳米管。其它制备方法还包括：将NaOH与商用TiO 2按照计量关系称量后移入聚四氟乙烯高压反应釜内，混合后在230℃温度下保温48h至96h，待冷却至室温后取出、洗涤、干燥后获得钛酸钠纳米管，并进一步酸洗得到钛酸纳米管。由此可见，传统的强碱水热法的特点在于：1)以TiO 2为钛源；2)在高压反应容器中进行，需要密闭高压条件；3)在较高温度进行；4)需要很长的反应时间才能首先破坏稳定的O-Ti键，然后重新形成O-Ti键，且反应时间以数十小时计算；5)得到的产物一般为钛酸盐纳米管或者钛酸纳米管。与此不同，本申请在制备含有纳米钛酸盐的纳米复合金属氧化物时，虽然也采用了强碱溶液，但与传统强碱水热法具有明显的不同：1)以含Ti的金属间化合物为钛源；2)反应可以在敞开容器与常压下进行，不一定需要高压密闭容器；3)优选在碱溶液的沸点温度附近进行，且温度的上限为碱溶液的沸点，非常容易精准控制；4)反应可以在几分钟甚至几十秒内完成。因此，本申请巧妙地将传统的氧化物原料改变为金属间化合物初始合金原料，极大地缩短了反应所需时间，提高了效率。
这一明显的有益效果，尤其是极大地缩短了目标产物的制备时间，与初始合金在较高的温度，尤其优选为碱溶液的沸点温度T f溶液的反应密切相关。当反应在常压下，且在碱溶液沸点温度发生时，反应体系的溶液组成具有明显特殊性，具体表现在：远在溶液沸点温度以下，溶剂主要以液态水存在；但在溶液沸点温度或者极其临近沸点温度时，溶剂中除了液态水与大量高活性气态水(沸点温度蒸发产生的气态水)外，还包含正在发生由液态水向气态水转变的高活性水。而且，这一特殊环境下，溶剂中溶解的大气环境气体(氧气、氮气)的含量与状态也极为特殊(因为水蒸气与氢气的大量出现，改变了水中溶解气体的饱和分压条件)。此外，A-T金属间化合物与浓碱溶液反应生成的大量氢气，以及溶于溶液中的少量盐都会改变反应体系的物质组成，这些都为反应提供了一个非常特殊的反应环境。这一特殊的反应环境，可以极大地缩短目标产物的制备时间。相比而言，例如传统高压水热法制备纳米钛酸盐薄膜采用稳定性极高的TiO 2为Ti源，需要通过高压、高温、长时间的反应才能首先破坏TiO 2的Ti-O键结构，只有Ti-O键破坏之后，才能进一步生成新的中间产物与最终产物，所需时间一般以数小时计算。而且，当溶液中碱的浓度确定时，其常压下溶液所能加热到的沸点温度也就确定了，也就意味着反应条件中的压力与温度就被精准确定。溶液沸点T f溶液温度下，溶液中任何补充的过多热量都会转变为水的汽化热而不会使溶液温度升高，这就可以通过持续加热保持溶液的温度恒定为沸点温度。即使反应过程中金属间化合物的析氢脱T过程产生大量的反应潜热，仍然可以保证反应溶液的温度维持在溶液的沸点温度。
第三，本申请其一方面发现，当A-T金属间化合物与一定温度与浓度的碱溶液反应，反应速率超过2μm/min时，尤其优选为碱溶液的沸点温度反应时，可以迅速完全破坏初始合金的形状，实现原初始合金的纳米碎化，同时经形状与成分重构生成纳米尺度的具有颗粒分散性的含M或(与)Ti的固态物质。与此不同，室温或较低温度条件下去合金制备的产物一般为纳米多孔金属氧化物或纳米多孔金属，其仍然保持反应前原初始合金颗粒的外形，包括其棱角形状等。如对比实施例1中，常压下，当(TiNb)Al 3金属间化合物初始合金粉末与10mol/L且为25℃的NaOH溶液反应2h(反应界面的平均推进速率低于0.5μm/min)，反应前后原初始合金粉末的形状大致不变，仍然为原破碎状且具有棱角的粉末状颗粒，且其微观结构上也不生成具有颗粒分散性的诸如纳米颗粒、纳米片或者纳米棒的产物，而是生成纳米多孔结构。且这种纳米多孔结构通过三维连续网状连接的方式构成与原初始合金粉末形状一致的外观形貌，其粒径大小仍然为初始合金粉末相当的大小，主要为数微米或者数十微米级。而本申请制备过程中，当初始合金粉末的平均粒径为10μm时，通过调控碱浓度与碱温度，经过超过2μm/min的反应速率发生纳米碎化后，所得产物是平均粒径不超过500nm的具有颗粒分散性的含M或(与)Ti的固态物质，其颗粒内部不含有纳米多孔的次级结构，且这些含M或(与)Ti的固态物质也是可以分散的，虽然可以软团聚在一起，但其不通过三维连续网络状结构紧密刚性连接在一起维持原初始合金的外形，包括其颗粒的棱角外形等。也就是说，通过本申请的制备方法，无论初始合金形状大小如何，通过析氢脱T反应过程中的纳米碎化，均得到可分散的纳米级的含M或(与)Ti的固态物质。因此，鉴于初始合金的粒径一般较大，如条带一般厚超过10μm，粉末颗粒平均粒径一般大于5μm，较低温度或常温下的A-T金属间化合物与碱溶液的反应一般仍然得到微米级的大颗粒的纳米多孔金属氧化物或纳米多孔金属，这些产物在很多需要颗粒细小且需要分散性的场合不能胜任；而本申请则实现了高分散性的纳米级的含M或(与)Ti的固态物质制备，具有明显的积极意义。
而且，在纳米碎化的同时发生形状重构。所述形状重构，是指析氢脱T反应得到的纳米尺度的产物，不是简单的对纳米多孔结构(ligament)的碎化，而是完全重构。如果低温析氢脱T反应得到的是纳米多孔结构，而高温氢脱T反应得到的产物只是简单的将纳米多孔结构碎化，则其只能称之为简单碎化，产物形貌即为碎化的多孔系带(ligament)。但本申请所述方案发生的并不是这种简单的碎化，而是还包括形状重构；含M或(与)Ti的固态物质的各种不同的形貌，如板条状结构、絮状结构，尤其是薄膜状结构，都不能简单地通过纳米多孔结构系带(ligament)的碎化获得。因此，本申请创造性地实现了含M或(与)Ti的固态物质不依托纳米多孔结构的形成机制形成并进一步简单碎化，而是通过特殊的碎化与完全重构过程形成。
第四，实现了含M中间产物与含Ti中间产物的原位嵌生复合，甚至也包括少部分含D中间产物与含M中间产物与(或)含Ti中间产物的原位嵌生复合。这种嵌生与普通的靠范德华力物理吸附主导的其它文献报道吸附结合不同(范德华力吸附的纳米颗粒可以移动、脱落)，其可以保证含M中间产物、含Ti中间产物，以及含D中间产物彼此可以紧密地嵌生在一起(不能移动、脱落)，从而获得更多的优异的性能。
第五，本申请发现，所述初始合金中的D类元素(Zr、Hf元素)，当其与热的浓碱溶液反应时，Zr、Hf元素可以溶解于热的浓碱溶液中，且这种溶解能力随着温度的升高明显增强。当反应在常压下，且在优选在碱溶液沸点温度发生反应时，这种溶解现象极为明显。这里所述溶解并不是狭义的溶解之意，而是特指含D类元素金属间化合物通过一系列反应后，以类似络合物的某种方式或其他未知方式溶解于过量的热浓碱溶液中。特别地，Zr、Hf元素的这种溶解特性，与碱溶液的浓度相关，当溶解有Zr、Hf元素的中间溶液的碱浓度降低后，含Zr、Hf的固态絮状物质氢氧化D就会析出来。这一发现，与传统的去合金法制备金属纳米多孔结构，以及传统去合金法制备纳米金属氧化物的情况均不同。在这些传统去合金反应过程中，反应物、中间产物及最终产物一直以固态形式存在，只是其成分与形貌不断变化而已。由于Zr、Hf元素可以溶于浓碱溶液中，且其从浓度降低的碱溶液中的析出是一个从无到有的过程，可以利用这一特点，通过后续降低碱溶液浓度的方式，或者加入表面活性剂的方式，获得极为细小的氢氧化D，具有极为明显的积极意义。当反应体系已经生成含M或(与)Ti的固态物质时，降低碱浓度诱发氢氧化D的析出，可以使得纳米氢氧化D极为均匀地与含M或(与)Ti的固态物质复合在一起。这种均匀复合，对后续材料制备如陶瓷烧结的产物性能极为重要，具有积极意义。
第六，实现了可分散与细化的晶态复合纳米金属氧化物的制备。例如，晶态纳米ZrO 2一直是先进陶瓷材料的关键原料。低成本的晶态纳米ZrO 2的制备方法主要是首先制备氢氧化锆前驱体(如通过氧氯化锆与氨水反应析出氢氧化锆絮状沉淀)，然后热处理烧结得到晶态ZrO 2，最后将烧结得到的晶态ZrO 2通过球磨或砂磨处理分散细化，得到先进陶瓷制品的重要原料晶态纳米ZrO 2粉体颗粒，且粉体颗粒越细，性能越优。目前，工业界一直没有解决的问题是：通过沉淀法获得的胶絮状氢氧化锆虽然极细，但其烧结后，往往得到大颗粒的烧结晶态纳米ZrO 2，且这种大颗粒ZrO 2非常致密(见对比实施例2图25-26)，难以通过后续球磨或砂磨分散细化到晶粒大小尺寸，实际只能得到数个或数十个晶粒组成的大颗粒ZrO 2(见对比实施例2图25-26)，这就极大地限制了晶态ZrO 2的低成本制备与应用。要想获得极细的晶态ZrO 2，目前工业界只能通过成本更高、产能更低、过程更复杂的高温高压水热法制备。而本申请则很好地解决了这个问题，例如，本申请首先制备氢氧化锆与含Ti中间产物或(与)含M中间产物的复合纳米金属与氧化物中间产物，使得后续高温烧结过程中，获得的含Ti中间产物或(与)含M中间产物掺杂复合的晶态ZrO 2具有很好的微观疏松特性与分散特性，其可以通过后续球磨或砂磨得到很好的分散细化，从而制备出单个或极少个晶粒组成的分散的通过掺杂复合的晶态ZrO 2(见实施例1图7-8)。这一技术，不仅很好地解决了烧结晶态ZrO 2的分散性与粒度问题，还通过原位复合使得参与复合的组分与晶态ZrO 2得到充分的均匀混合。例如，当复合组分包括Cr 2O 3(高端耐火材料的原料，也常作为高端绿色无机颜料)时，其不仅可显著提高ZrO 2-Cr 2O 3陶瓷制品的耐热温度，还可以获得着色效果。
第七，可以制备热稳定性或(与)晶化温度提高的复合纳米金属氧化物中间产物，以及颗粒疏松性或比表面积提高的复合纳米金属氧化物。
第八，本申请其一至其四方面任一方面所述制备方法制备的复合纳米金属氧化物或中间产物在制备过程中已经进行了充分的混合，尤其是原位嵌生对应的混合，其极大地降低了所述复合纳米金属氧化物各组分之间均匀混合所需要的成本。
总之，本发明所涉及的技术方案中，反应时间为数十秒到数分钟；反应条件可以精准控制并可以迅速终止反应。这些特点都极大地简化了生产过程，提高了生产效率，并降低了生产成本，使相应产物材料的低成本大规模制备成为了可能。因此，本发明所涉及的技术方案与制备方法具有工艺简单、易于控制、效率高、成本低的特点，可以制备包括多种复合纳米金属氧化物，适宜在复合材料、催化材料、陶瓷材料、耐火材料、先进电子材料、电池材料、变色材料、吸波材料、污水降解材料、杀菌材料、涂料、颜料、热喷涂材料、传感器中应用。
附图说明
图1为实施例1初始合金凝固组织的低倍SEM照片；
图2为实施例1初始合金凝固组织的高倍SEM照片；
图3为实施例1制备的复合纳米金属氧化物中间产物的低倍TEM照片与衍射谱；
图4为实施例1制备的复合纳米金属氧化物中间产物的中倍、高倍TEM照片；
图5为实施例1制备的600℃热处理后的复合纳米金属氧化物的低倍TEM照片与衍射谱；
图6为实施例1制备的600℃热处理后的复合纳米金属氧化物的中倍、高倍TEM照片；
图7为实施例1制备的900℃热处理后的复合纳米金属氧化物的低倍TEM照片与衍射谱；
图8为实施例1制备的900℃热处理后的复合纳米金属氧化物的中倍、高倍TEM照片；
图9为实施例2初始合金凝固组织的SEM照片；
图10为实施例2制备的复合纳米金属氧化物中间产物、650℃热处理、900℃热处理的复合纳米金属氧化物的XRD谱；
图11为实施例3制备的复合纳米金属氧化物中间产物的低倍TEM照片与衍射谱；
图12为实施例3制备的复合纳米金属氧化物中间产物的高倍TEM照片；
图13为实施例3制备的900℃热处理后的复合纳米金属氧化物的低倍TEM照片；
图14为实施例3制备的900℃热处理后的复合纳米金属氧化物的中倍、高倍TEM照片；
图15为实施例4制备的复合纳米金属氧化物中间产物的低倍TEM照片与衍射谱；
图16为实施例4制备的复合纳米金属氧化物中间产物的高倍TEM照片；
图17为实施例5制备的复合纳米金属氧化物中间产物的低倍TEM照片与衍射谱；
图18为实施例5制备的1100℃热处理后的复合纳米金属氧化物的中倍、高倍TEM照片；
图19为实施例6制备的复合纳米金属氧化物中间产物的低倍TEM照片与衍射谱；
图20为对比实施例1所得产物的低倍、高倍SEM照片；
图21为对比实施例2制备的低结晶度的纳米氢氧化Zr的低倍TEM照片与衍射谱；
图22为对比实施例2制备的低结晶度的纳米氢氧化Zr的高倍TEM照片；
图23为对比实施例2制备的600℃热处理后的纳米氧化Zr的低倍TEM照片与衍射谱；
图24为对比实施例2制备的600℃热处理后的纳米氧化Zr的高倍TEM照片；
图25为对比实施例2制备的900℃热处理后的纳米氧化Zr的低倍TEM照片与衍射谱；
图26为对比实施例2制备的900℃热处理后的纳米氧化Zr的高倍TEM照片。
具体实施方式
以下，将通过以下具体实施例对所述技术方案做进一步的说明：
实施例1
本实施例提供一种包含Zr、Nb与Ti元素的复合纳米金属氧化物及复合氧化物陶瓷的制备方法，包括如下步骤：
按照Al 75Zr 18Ti 4Nb 3(原子百分比)的名义配比称取金属Nb、Zr、Ti、Al原料，熔炼得到成分主要为Al 75Zr 18Ti 4Nb 3的合金熔体，然后将该合金熔体凝固成合金锭，并将其破碎成平均粒径100μm的初始合金粉末，其凝固组织相 组成主要由成分约为Al 73Zr 20Ti 3Nb 4与Al 76Zr 13Ti 10Nb 1的两个金属间化合物组成，且以成分约为Al 73Zr 20Ti 3Nb 4的金属间化合物为主，如图1与图2所示的合金锭凝固组织的SEM图。其中，Al 73Zr 20Ti 3Nb 4的金属间化合物可能为固溶有Ti与Nb的Al 3Zr相；Al 76Zr 13Ti 10Nb 1的金属间化合物可能为固溶有Nb的Al 3(Zr-Ti)相；
常压下，将4g的Al 75Zr 18Ti 4Nb 3初始合金粉与NaOH水溶液反应，并不断搅拌；其中，NaOH溶液的浓度为12mol/L，温度为其常压下的沸点温度(～128℃)，NaOH溶液的体积为300ml；2min之内，析氢脱Al反应结束，Al 75Zr 18Ti 4Nb 3初始合金粉通过析氢脱Al反应发生纳米碎化，并同时经形状与成分重构生成含Ti、Nb以及少量Zr的固态絮状物质，而大部分Zr则主要溶于碱溶液中；当生成固态絮状物质时，其微观上由大量极小的絮状微结构软团聚而成，单个微结构的尺度远远小于20nm；
析氢脱Al反应开始3min后，在剧烈搅拌状态下，将3000ml常温水在1min内缓慢加入所述反应体系中，使得碱溶液的浓度降低到2mol/L以下，同时碱溶液温度降低到40℃以下；在碱溶液浓度降低的过程中，原溶于碱溶液中的大部分Zr元素以固态胶絮状氢氧化Zr的方式形核析出，并均匀地与反应体系中已经生成的含Ti与Nb的固态物质混合；
将上述固液分离，收集所有固态絮状物质，经稀酸清洗至PH＝4-5，然后干燥，即得到主要由低结晶的氢氧化Zr与含Ti、Nb的固态絮状物质均匀复合的复合纳米金属氧化物中间产物；其低倍、中倍、高倍TEM形貌及衍射谱如图3-4所示；由图3可见，所述复合纳米金属氧化物中间产物团聚体的平均粒度低于250nm，由图4的高倍照片插图可见，复合纳米金属氧化物中间产物团聚体由更为细小的絮状微结构组成，其组成主要为胶絮状氢氧化Zr，由于团聚体为非晶态，因此难以观察到微结构的细节。由于单纯Al-Nb金属间化合物在上述反应条件下得到的也是胶絮状氢氧化Nb或非晶态氧化Nb，因此不能从图3-4中将其与胶絮状氢氧化Zr通过TEM衬度区分出来；由于Ti在初始合金中占Zr、Ti、Nb的总摩尔百分含量较少，且Nb与Ti的摩尔百分含量几乎相当，含Ti中间产物与含Nb中间产物在析氢脱Al反应过程中同时生成时，含Ti中间产物未能以二维纳米钛酸盐薄膜的方式形成(单纯Al-Ti金属间化合物在上述反应条件下得到的是厚度0.5nm-4nm的二维纳米钛酸纳薄膜，酸洗后变成厚度0.5nm-4nm的二维纳米钛酸薄膜)；据此可以判断，含Ti中间产物与含Nb中间产物在生成的同时发生了充分的复合作用，其可能以含Ti/Nb的某种胶絮状中间产物存在，且与胶状氢氧化Zr难以区分衬度。其中，含Ti中间产物、Nb中间中间产物，以及少量同时在先生成的含Zr中间产物在原子或原子团簇的尺度发生了原位嵌生复合。
将上述复合纳米金属氧化物中间产物在600℃下热处理2h，即得到少部分晶化的复合纳米金属氧化物；其低倍、中倍、高倍TEM形貌及衍射谱如图5-6所示；可见，所述少部分晶化的复合纳米金属氧化物团聚体的平均粒度低于150nm(胶絮状团聚体发生了收缩)。结合对比实施例2，单纯Al 3Zr金属间化合物在按照本实施例的相似条件反应首先的得到是胶絮状的纳米氢氧化Zr(如图21-22所示)，其形貌边界较为模糊；当单纯的胶絮状的纳米氢氧化Zr在600℃下热处理2h后，得到的是明显晶化的纳米二氧化Zr，如图23更为清晰分层的衍射环，以及图24高倍形貌下图22原来模糊的胶絮状形貌边界变成了清晰的白亮形貌边界。通过对比可以确认，本实施例获得的以氢氧化Zr为主的复合纳米金属氧化物中间产物的热稳定性与晶化温度得到了明显的提高，即相对于相似条件制备的单纯的胶絮状氢氧化Zr，其更难发生晶化。这进一步说明在先析出的含Ti中间产物、含Nb中间产物、少量含Zr中间产物、以及后析出的纳米氢氧化Zr中间产物组成的热处理之前的复合纳米金属氧化物中间产物各组分之间进行了与化学交互作用相关的原位嵌生复合，且这种原位嵌生复合特征保留到600℃下热处理2h后的产物中。
将上述复合纳米金属氧化物中间产物在900℃下热处理2h，即得到以纳米氧化锆为主的晶态的复合纳米金属氧化物；其低倍、中倍、高倍TEM形貌及衍射谱如图7-8所示；可见，所述晶态复合纳米金属氧化物的平均粒度低于100nm(进一步发生了烧结收缩)，且这些颗粒之间虽然发生了一定的烧结团聚，但其仍然维持一种疏松的烧结团聚状态，或者说是一种类似纳米多孔的结构，表现为由大量直径20nm-40nm的条状结构组成，这种结构使得所制备的复合纳米金属氧化物具有较高的颗粒疏松性或比表面积。结合对比实施例2，单纯Al 3Zr金属间化合物在按照本实施例的相似条件反应首先的得到的胶絮状的纳米氢氧化Zr(如图21-22所示)；当单纯的胶絮状的纳米氢氧化Zr在900℃下热处理2h后，得到的是晶化的纳米氢氧化Zr，见图25-26所示。但其虽然为多晶颗粒，但其烧结团聚成了实心的大颗粒，完全失去了颗粒的疏松性，也呈现低的比表面积。由于氧化锆本身强度高，这种实心的大颗粒几乎不能通后续砂磨、球磨手段碎化。因此，通过对比可以确认，本实施例获 得的纳米氧化锆为主的含Ti、Nb元素的晶态复合纳米金属氧化物具有较高的颗粒疏松性或比表面积，解决了烧结得到的单纯纳米氧化锆难以进一步将其破碎细化的工业界难题。这也进一步说明在先析出的含Ti中间产物、含Nb中间产物、少量含Zr中间产物、以及后析出的纳米氢氧化Zr中间产物组成的热处理之前的复合纳米金属氧化物中间产物各组分之间进行了与化学交互作用相关的原位嵌生复合，且这种原位嵌生复合特征保留到900℃下热处理2h后的产物中。
通过砂磨的方式，将上述以纳米氧化锆为主的含Ti、Nb元素的晶态复合纳米金属氧化物破碎为粒径为20nm-40nm的晶态复合纳米金属氧化物粉末(该粒径即为破碎之前复合纳米金属氧化物条状结构的直径范围)。
将所得晶态复合纳米金属氧化物粉末混匀后在50MPa压力下压制成为坯体，经1400℃焙烧2h，即得到摩尔比Zr：Ti：Nb约为18：4：3的以氧化锆为主的复合纳米氧化物陶瓷。
将所得晶态复合纳米金属氧化物粉末与纳米Al 2O 3粉末按照摩尔比1:3的比例混合，湿法球磨混匀处理后烘干，即得到混合均匀的混合粉料；将混合粉料在50MPa压力下压制成为坯体，经1400℃焙烧2h，即得到由氧化铝进一步复合的复合纳米氧化物陶瓷。
实施例2
本实施例提供一种包含Zr与Y元素的复合纳米金属氧化物及复合氧化物陶瓷的制备方法，包括如下步骤：
按照Al 75Zr 23.5Y 1.5(原子百分比)的名义成分配比称取Zr、Y、Al原料，熔炼得到成分主要为Al 75Zr 23.5Y 1.5的合金熔体，然后将该合金熔体凝固成合金锭，并将其破碎成平均粒径50μm的初始合金粉末，其相组成主要由Al 3Zr与Al 3Y金属间化合物组成，如图9所示；
常压下，将3g上述制得的初始合金条带与200mL浓度为10mol/L，温度为其沸点温度(119℃)的NaOH水溶液反应，并不断搅拌。1.5min内，析氢脱Al反应结束，初始合金与所述碱溶液通过剧烈的析氢脱Al反应发生纳米碎化，并进一步经形状与成分重构生成主要含Y的固态物质，同时，原初始合金中绝大多数Zr则溶于所述碱溶液中；
析氢脱Al反应开始3min后，将常温水缓慢加入所述反应体系中，使得碱溶液的浓度降低到1mol/L以下，同时碱溶液温度降低到40℃以下；胶絮状的氢氧化Zr从浓度降低后的碱溶液中形核析出，并均匀地与碱溶液中已经生成的含Y固态物质混合；
经固液分离，收集含Y与Zr的混合胶絮状固态物质，经稀酸清洗、干燥，即得到由纳米氧化钇与低结晶度胶絮状氢氧化Zr组成的复合纳米金属氧化物中间产物，且两者主要通过物理吸附的方式均匀地复合在一起；其中，纳米氧化钇的粒径范围为3nm～200nm；胶絮状氢氧化Zr的絮状微结构的粒径为0.5nm-10nm；该复合纳米金属氧化物中间产物中不含有三维连续网络状的纳米多孔结构或多孔骨架结构；该复合纳米金属氧化物中间产物的XRD如图10所示，由于氧化钇含量较少，其XRD峰仅仅显示低结晶度氢氧化Zr的衍射信息。
将上述含Y与Zr的复合纳米金属氧化物中间产物在650℃下热处理1.5h，即得晶态纳米氧化钇与部分晶态纳米氧化锆均匀复合的复合纳米金属氧化物；其中，晶态纳米氧化钇的粒径范围为3nm～200nm；部分晶态纳米氧化锆的粒径范围为3nm～200nm；该复合纳米金属氧化物的XRD如图10所示，由于纳米氧化Zr未有完全晶化，峰强度还不太明显，且由于氧化钇含量较少，其XRD峰不明显。
将上述含Y与Zr的复合纳米金属氧化物中间产物在900℃下热处理1.5h，即得主要由氧化Zr组成的含氧化Y的复合纳米金属氧化物；其粒径低于250nm，其XRD如图10所示，可见氧化锆晶化明显，峰强度也明显，由于氧化钇含量较少，其XRD峰不明显。
将上述900℃下热处理1.5h后的复合纳米金属氧化物在30MPa压力下压制成为坯体，经1450℃焙烧2h，即制得氧化钇稳定氧化锆的复合纳米氧化物氧化物陶瓷，其中摩尔比Zr：Y约为23.5：1.5。
将上述900℃下热处理1.5h后的复合纳米金属氧化物与纳米Al 2O 3粉末按照摩尔比4:1的比例混合，湿法球磨混匀处理后烘干，即得到混合均匀的混合粉料；将混合粉料在50MPa压力下压制成为坯体，经1450℃焙烧2h，即得含有氧化铝、氧化钇、氧化锆的复合纳米氧化物陶瓷。
实施例3
本实施例提供一种包含Hf与Cr元素的复合纳米金属氧化物及复合氧化物陶瓷的制备方法，包括如下步骤：
按照Al 75Hf 20Cr 5(原子百分比)的名义配比称取金属Hf、Cr、Al原料，熔炼得到成分主要为Al 75Hf 20Cr 5的合金熔体，然后将该合金熔体通过熔体甩带法制备成厚度20μm-30μm的Al 75Hf 20Cr 5初始合金条带，其相组成主要由含有Cr的Al 3Hf(Cr)金属间化合物组成。
常压下，将1g的Al 75Hf 20Cr 5初始合金条带与KOH水溶液反应，并不断搅拌；其中，KOH溶液的浓度为10mol/L，温度为其常压下的沸点温度(～125℃)，KOH溶液的体积为100ml；1min之内，析氢脱Al反应结束，Al 75Hf 20Cr 5初始合金条带通过析氢脱Al反应发生纳米碎化，并同时经形状与成分重构生成主要含Cr及少部分Hf的固态胶絮状物质，而大部分Hf则主要溶于碱溶液中；
析氢脱Al反应开始2min后，在剧烈搅拌状态下，将1000ml常温水在1min内缓慢加入所述反应体系中，使得碱溶液的浓度降低到1mol/L以下，同时碱溶液温度降低到40℃以下；在碱溶液浓度降低的过程中，原溶于碱溶液中的大部分Hf元素以固态胶絮状氢氧化Hf的方式形核析出，并均匀地与反应体系中已经生成的主要含Cr的固态胶絮状物质混合；
将上述固液分离，收集所有固态物质，经稀酸清洗至PH＝4-5，然后干燥，即得到主要由低结晶的氢氧化Hf与主要含Cr的固态絮状物质均匀复合的复合纳米金属氧化物中间产物；其TEM形貌及衍射谱如图11-12所示；由图可见，所述复合纳米金属氧化物中间产物团聚体的平均粒度低于200nm，且复合纳米金属氧化物中间产物团聚体由更为细小的絮状微结构组成，其组成主要为胶絮状氢氧化Zr中间产物，以及与之复合的胶絮状氢氧化Cr或胶絮状氧化Cr中间产物。由于单纯Al-Cr金属间化合物在上述反应条件下得到的也是胶絮状氢氧化Cr或非晶态氧化Cr，因此不能从图11-12中将其与胶絮状氢氧化Hf通过TEM衬度区分出来；
将上述复合纳米金属氧化物中间产物在900℃下热处理2h，即得到以纳米氧化Hf为主的通过氧化Cr复合的晶态的复合纳米金属氧化物；其低倍、中倍、高倍TEM形貌如图13-14所示；可见，所述晶态复合纳米金属氧化物的平均粒度低于50nm，且这些颗粒之间虽然发生了一定的烧结团聚，但其仍然维持一种疏松的烧结团聚状态，或者说是一种类似纳米多孔的结构，表现为由大量直径15nm-40nm的条状结构组成，这种结构使得所制备的复合纳米金属氧化物具有较高的颗粒疏松性或比表面积。该疏松结构解决了烧结得到的单纯纳米氧化Hf难以进一步将其破碎细化的工业界难题。这种缩松性结构的存在，说明在烧结之前，胶絮状氢氧化Zr中间产物与氢氧化Cr(或氧化Cr)中间产物之间在极小的尺度发生了均匀复合，其这种均匀复合在烧结过程中演变成为了烧结诱导的原位嵌生复合，从而改变了其烧结后产物的形貌与烧结特性，获得了具有较高的颗粒疏松性或比表面积的晶态复合纳米金属氧化物。
通过砂磨的方式，将上述以纳米氧化Hf为主的通过氧化Cr复合的晶态复合纳米金属氧化物破碎为粒径为15nm-40nm的晶态复合纳米金属氧化物粉末。
将所得晶态复合纳米金属氧化物粉末混匀后在50MPa压力下压制成为坯体，经1250℃焙烧2h，即得到摩尔比Hf：Cr约为5：1的以氧化Hf为主的通过氧化Cr复合的复合纳米氧化物陶瓷。
实施例4
本实施例提供一种包含Ti与Ta元素的复合纳米金属氧化物及其制备方法，包括如下步骤：
按照Al 75Ti 22Ta 3(原子百分比)的名义配比称取金属Ti、Ta、Al原料，熔炼得到成分主要为Al 75Ti 22Ta 3的合金熔体，然后将该合金熔体通过熔体甩带法制备成厚度20μm-30μm的Al 75Ti 22Ta 35初始合金条带，其相组成主要由含有Ta的Al 3Ti(Ta)金属间化合物组成。
常压下，将0.5g的Al 75Ti 22Ta 3初始合金条带与NaOH水溶液反应，并不断搅拌；其中，NaOH溶液的浓度为7mol/L，温度为其常压下的沸点温度(～112℃)，NaOH溶液的体积为100ml；2min之内，析氢脱Al反应结束，Al 75Ti 22Ta 3初始合金条带通过析氢脱Al反应发生纳米碎化，并同时经形状与成分重构生成含Ti与Ta的固态絮状物质；
析氢脱Al反应开始3min后，将上述固液分离，收集固态絮状物质，即得到Ta元素参与复合的主要由低结晶度纳米钛酸钠组成的复合纳米金属氧化物中间产物；其中，含Ti中间产物为纳米钛酸钠基体，其形状主要为薄膜状，且薄膜厚度为0.5nm-5nm，薄膜平均面积大于200nm 2；含Ta中间产物为纳米氧化Ta，其通过原位嵌生复合的方式镶嵌生长在纳米钛酸钠薄膜中，且其粒径为0.5nm-5nm。
将上述Ta元素参与复合的主要由低结晶度纳米钛酸钠组成的复合纳米金属氧化物中间产物通过0.05mol/L的稀盐酸酸洗至PH＝4-5，然后干燥，即得到由Ta元素参与复合的主要由低结晶度纳米钛酸组成的复合纳米金 属氧化物中间产物；其TEM形貌及衍射谱如图15-16所示；由衍射图可见，所得复合纳米金属氧化物中间产物仍然为低结晶态；此时，酸洗之前的纳米钛酸钠基体变成了纳米钛酸基体，其形状仍然主要为薄膜状(见图15，尤其图片下部的超薄薄膜)，且薄膜厚度为0.5nm-5nm，薄膜平均面积大于200nm 2；含Ta中间产物仍然为纳米氧化Ta，其通过原位嵌生复合的方式镶嵌生长在稍厚一点的纳米钛酸薄膜中(如图16所示)，且其粒径为0.5nm-5nm。
将上述Ta元素参与复合的主要由低结晶度纳米钛酸组成的复合纳米金属氧化物中间产物在900℃下热处理2h，即得到氧化Ta参与复合的以纳米TiO 2为主的复合纳米金属氧化物。烧结过程中，钛酸薄膜演化成厚度为2nm-20nm，平均面积大于100nm 2的板片状晶态纳米TiO 2；同时纳米氧化Ta原位嵌生复合在板片状晶态纳米TiO 2中。
实施例5
本实施例提供一种包含Zr、Hf、Ti与Cr元素的复合纳米金属氧化物及其制备方法，包括如下步骤：
按照Al 61Cr 34Zr 3Hf 1Ti 1(原子百分比)的名义配比称取金属Zr、Hf、Ti、Cr、Al原料，熔炼得到成分主要为Al 61Cr 34Zr 3Hf 1Ti 1的合金熔体，然后将该合金熔体凝固成厚度100μm-200μm的Al 61Cr 34Zr 3Hf 1Ti 1初始合金速凝片，其相组成主要由固溶有Zr、Hf、Ti的Al 8Cr 5金属间化合物组成。
常压下，将3g的Al 61Cr 34Zr 3Hf 1Ti 1初始合金速凝片与NaOH水溶液反应，并不断搅拌；其中，NaOH溶液的浓度为12mol/L，温度为其常压下的沸点温度(～128℃)，NaOH溶液的体积为300ml；3min之内，析氢脱Al反应结束，Al 61Cr 34Zr 3Hf 1Ti 1初始合金速凝片通过析氢脱Al反应发生纳米碎化，并同时经形状与成分重构生成含Cr、Ti、Hf、Zr的固态絮状物质，其中大部分Hf、Zr溶于碱溶液中。由于Hf、Zr所占摩尔比较少，且其在金属间化合物中与Cr、Ti在原子尺度均匀分散分布，因此，含Cr、Ti的固态絮状物质形成时，少部分Hf、Zr也以原子或原子团簇的方式原位嵌生于其中；
析氢脱Al反应开始4min后，在剧烈搅拌状态下，将3000ml常温水在1min内缓慢加入所述反应体系中，使得碱溶液的浓度降低到1.5mol/L以下，同时碱溶液温度降低到40℃以下；在碱溶液浓度降低的过程中，原溶于碱溶液中的大部分Hf、Zr以固态胶絮状氢氧化Zr/Hf的方式形核析出，并均匀地与反应体系中已经生成的含Cr、Ti、Hf、Zr的固态絮状物质混合；
将上述固液分离，收集所有固态絮状物质，经稀酸清洗至PH＝4-5，然后干燥，即得到Ti、Hf、Zr参与复合的主要由低结晶的氧化Cr或氢氧化Cr组成的复合纳米金属氧化物中间产物；其TEM形貌及衍射谱如图17所示。可见，其主要为低结晶态，且其细节主要由絮状微结组成，且絮状微结构的粒径为0.5nm-5nm。该复合纳米金属氧化物中间产物中，Ti中间产物与少部分Hf、Zr中间产物通过原位嵌生复合与氧化Cr或氢氧化Cr中间产物复合；这种原位嵌生复合包括原子或原子团簇尺度的复合，也包括细相尺度的复合。
将上述复合纳米金属氧化物中间产物在1100℃下热处理2h，即得到Ti、Hf、Zr的氧化物参与复合的以纳米氧化Cr为主的晶态的复合纳米金属氧化物；其TEM形貌如图18所示；由图可见，虽然热处理温度高达1100℃，仍然可以获得疏松烧结团聚状态的复合纳米金属氧化物，其颗粒粒径范围为30nm-150nm；虽然各个颗粒之间发生了一定的烧结团聚，但这种类似纳米多孔的结构很容易通过后续球磨、砂磨过程进行破碎细化。
通过砂磨的方式，将上述Ti、Hf、Zr的氧化物参与复合的以纳米氧化Cr为主的晶态的复合纳米金属氧化物破碎为粒径为30nm-150nm的晶态复合纳米金属氧化物粉末。
将所得晶态复合纳米金属氧化物粉末混匀后在50MPa压力下压制成为坯体，经1400℃焙烧2h，即得到摩尔比Cr：Zr：Hf：Ti约为34：3：1：1，通过Ti、Hf、Zr的氧化物进行复合的氧化铬基耐火材料。
实施例6
本实施例提供一种包含Ti与Mn元素的复合纳米金属氧化物的制备方法，包括如下步骤：
按照Zn 67Ti 28Mn 5(原子百分比)的名义配比称取金属Ti、Mn、Zn原料，熔炼得到成分为Zn 67Ti 28Mn 5的合金熔体，然后将该合金熔体凝固成合金锭，并将其破碎成平均粒径50μm的初始合金粉末，其相组成主要由Zn 2Ti金属间化合物与Zn-Mn金属间化合物组成；
常压下，将0.5g上述制得的初始合金条带与50mL温度为105℃-115℃的摩尔比为1:1的KOH与NaOH溶液反应，并不断搅拌，碱液中OH -的浓度为15mol/L；2min内，初始合金粉末与所述碱溶液通过剧烈的析氢脱 Zn反应发生纳米碎化，并进一步经形状与成分重构生成含Mn与Ti的固态絮状物质；
析氢脱Zn反应开始4min后，将上述包含有固态絮状物质的热碱溶液倾倒在与水平面呈45度角的且孔径分别为1mm、200μm、20μm、5μm的四叠层铜网上，固态絮状物质被保留在四叠层铜网上，碱溶液则被滤掉。
收集含Mn与Ti的固态絮状物质，经0.01mol/L盐酸酸洗至PH＝4-5，经干燥，即得到Mn参与复合的主要由纳米钛酸组成的复合纳米金属氧化物中间产物，如图19所示，其形状主要为低结晶度的薄膜状，其中薄膜厚度为0.25nm～5nm，单片膜的平均面积大于500nm 2；结合单纯Zn 2Ti金属间化合物或单纯Zn-Mn金属间化合物在该反应条件下均有生成薄膜状产物的趋势，因此，难以通过TEM形貌与衬度区分含Ti中间产物与含Mn中间产物。考虑到Ti中间产物与含Mn中间产物同时形成，因此，其必然彼此之间存在一定程度的原位嵌生复合关系，包括原子或原子团簇尺度的原位嵌生复合。
将上述Mn参与复合的主要由纳米钛酸组成的复合纳米金属氧化物中间产物在900℃下热处理1.5h，纳米钛酸膜转化为纳米TiO 2片，即得到晶态纳米氧化锰与红石型纳米TiO 2片复合的复合纳米金属氧化物，其中纳米TiO 2片的厚度为3nm～20nm，平均面积大于150nm 2；晶态纳米氧化锰的粒径为3nm～20nm；且晶态纳米氧化锰与金红石型纳米TiO 2片的主要复合方式包含原位嵌生复合。
实施例7
本实施例提供一种包含Cr与Ti元素的复合纳米金属氧化物及其制备方法，包括如下步骤：
按照Al 61Cr 35Ti 4(原子百分比)的名义配方，通过Al、Cr与Ti原料熔炼得到成分主要为Al 61Cr 35Ti 4的合金熔体，将该合金熔体通过铜辊甩带速凝的方法制备成厚度为20μm～30μm，成分主要为Al 61Cr 35Ti 4的初始合金条带，其凝固组织主要由固溶有Ti的Al 8Cr 5(Ti)金属间化合物组成。
常压下，将Al 61Cr 35Ti 4初始合金条带与NaOH水溶液反应，并辅以40kHz超声处理；其中，NaOH溶液的浓度为15mol/L，温度为60℃，NaOH溶液的体积为Al 61Cr 35Ti 4初始合金条带体积的约100倍；Al 61Cr 35Ti 4初始合金条带与NaOH溶液的反应速率大于2μm/min，8min之内，析氢脱Al反应结束，初始合金通过析氢脱Al反应发生纳米碎化，并同时经形状与成分重构生成固态胶絮状中间产物；
析氢脱Zn反应开始10min后，将固态胶絮状中间产物与溶液分离，经0.01mol/L盐酸酸洗至PH＝4-5、经干燥，即得到Ti参与复合的主要由低结晶态纳米氢氧化Cr或纳米氧化Cr组成的复合纳米金属氧化物中间产物；其形貌为胶絮状，且絮状微结构的粒径大小为0.5nm-10nm，由于初始合金中Ti含量相对Cr含量较少，含Ti中间产物未以钛酸盐或钛酸薄膜的方式出现，其主要通过原位嵌生复合的方式存在于低结晶态纳米氢氧化Cr或纳米氧化Cr中间产物中；
将上述Ti参与复合的主要由低结晶态纳米氢氧化Cr或纳米氧化Cr组成的复合纳米金属氧化物中间产物在1000℃下热处理2h，低结晶态纳米氢氧化Cr或纳米氧化Cr则转化为晶态氧化Cr颗粒，其粒径大小为3nm-150nm；同时，含Ti组分主要通过原位嵌生复合的方式存在于晶态氧化Cr中。
实施例8
本实施例提供一种包含Ti、Ta元素的复合纳米金属氧化物的制备方法，包括如下步骤：
按照Al 74Ti 21Ta 5(原子百分比)的名义配比称取金属Ti、Ta、Al原料，熔炼得到成分为Al 74Ti 21Ta 5的合金熔体，然后将该合金熔体通过铜辊甩带速凝的方法制备成厚度为～25μm的初始合金条带，其相组成主要由固溶有Ta元素的Al 3Ti(Ta)金属间化合物组成。
常温常压下，将0.5g上述制得的初始合金条带与50mL浓度为10mol/L，温度为常温的NaOH水溶液混合，然后直接将混合好的碱溶液及碱溶液中的固态物质一起置于内衬为聚四氟乙烯的密封反应釜中；将密封反应釜及其内部的温度在10min内升高到200℃并保温30min；
保温30min后，将反应釜降温到常温后，将釜内压力恢复到常压，然后将反应釜内的固态物质与溶液分离、经稀酸清洗至PH＝4-5，然后干燥，即得到由含Ta中间产物与钛酸纳米管中间产物组成的复合纳米金属氧化物中间产物；其为部分结晶态；其中，钛酸纳米管中间产物的外径范围为5nm～15nm，长径大于5；含Ta中间产物主要为粒径范围为3nm～50nm的纳米氧化钽；钛酸纳米管与纳米氧化钽之间的复合方式包括原位嵌生复合，且该复合纳米金属氧化物中间产物中不含有三维连续网络状的纳米多孔结构或多孔骨架结构；
将上述含Ta中间产物与钛酸纳米管中间产物组成的复合纳米金属氧化物中间产物在1000℃下热处理2h，即得到晶态纳米氧化钽与金红石型晶态TiO 2棒组成的复合纳米金属氧化物。其中，金红石型晶态TiO 2棒的外径范围为6nm～25nm，长径大于3；晶态纳米氧化钽的粒径范围为3nm～50nm；金红石型晶态TiO 2棒与纳米氧化钽之间的复合方式包括原位嵌生复合。
实施例9：
本实施例提供一种包含Nb、Zr、Hf与Ti元素，且含有钛酸盐纳米管的复合纳米金属氧化物的制备方法，包括如下步骤：
Zn 75Ti 5Hf 5Zr 5Nb 5Mn 5(原子百分比)的名义配比称取金Zr、Hf、Ti、Nb、Mn、Zn原料，熔炼得到成分为Zn 75Ti 5Hf 5Zr 5Nb 5Mn 5的合金熔体，然后将该合金熔体通过铜辊甩带速凝的方法制备成厚度为～25μm的初始合金条带，其相组成主要由Zn与Zr、Hf、Ti、Nb、Mn的金属间化合物组成。
常温常压下，将0.5g上述制得的Zn 75Ti 5Hf 5Zr 5Nb 5Mn 5初始合金条带与50mL浓度为15mol/L，温度为常温的KOH水溶液混合，然后将混合好的碱溶液及碱溶液中的固态物质一起置于内衬为聚四氟乙烯的密封反应釜中；将密封反应釜及其内部的温度在10min内升高到250℃并保温1h；
保温1h后，将反应釜降温到常温后，将釜内压力恢复到常压，然后将反应釜内反应体系的碱溶液通过加水稀释至1mol/L以下，通过固液分离，经稀酸清洗至PH＝4-5、干燥，即得到包含Zr、Hf、Ti、Nb、Mn等元素复合的复合纳米金属氧化物中间产物；其平均粒径小于200nm，其为部分晶态，平均结晶度超过20％；其中，含Ti中间产物、含Nb中间产物、含Mn中间产物，以及少部分含Zr/Hf中间产物之间彼此的复合方式包括原位嵌生复合。大部分碱液稀释过程中析出的含Zr/Hf中间产物与在先析出的固态中间产物之间的复合主要为物理吸附复合；
将包含Zr、Hf、Ti、Nb、Mn等元素的复合的复合纳米金属氧化物中间产物在1000℃下热处理2h，即得到完全晶态的通过Zr、Hf、Ti、Nb、Mn等元素的氧化物复合的复合纳米金属氧化物，不同金属元素对应的组分之间的摩尔比约为等摩尔比，其中不同金属元素对应的组分之间复合的方式包括原位嵌生复合，其包括在原子或原子团簇尺度的原位嵌生复合或细相尺度的原位嵌生复合。
该方案可以不用单独制备这些金属元素的氧化物再混合，而是可以在合金设计的时候就设计好各个金属的比例，通过这个比例就可计算出各个金属对应的氧化物的含量。通过后续析氢脱T及后续处理，就可以得到部分结晶的通过Zr、Hf、Ti、Nb、Mn等元素的氧化物复合的复合纳米金属氧化物中间产物；其在制备过程即进行了原子/原子团簇尺度或细相尺度的原位嵌生复合；通过进一步热处理，即可得到充分复合的多组元复合纳米金属氧化物。
实施例10
本实施例提供一种包含Cr与Ti元素的复合纳米金属氧化物及其制备方法，包括如下步骤：
按照Al 61Cr 35Ti 4(原子百分比)的名义配方，通过Al、Cr与Ti原料熔炼得到成分主要为Al 61Cr 35Ti 4的合金熔体，将该合金熔体通过铜辊甩带速凝的方法制备成厚度为20μm～30μm，成分主要为Al 61Cr 35Ti 4的初始合金条带，其凝固组织主要由固溶有Ti的Al 8Cr 5(Ti)金属间化合物组成。
常压下，将0.5g上述制得的Al 61Cr 35Ti 4初始合金条带与50ml浓度为10mol/L的NaOH水溶液置于密闭容器中，一开始初始合金条带与碱溶液不接触；
将密闭容器内的温度，以及初始合金条带与碱溶液的温度升高到150℃，此时密闭容器内处于高压状态，然后将密闭容器内的Al 61Cr 35Ti 4初始合金条带与该温度的碱溶液混合，使之发生剧烈的析氢脱T反应，Al 61Cr 35Ti 4初始合金条带在高温高压反应过程中通过剧烈的析氢脱Al反应发生纳米碎化，并同时经形状与成分重构生成固态絮状产物。
析氢脱Al反应在10s内结束，10s之后，将密闭容器及反应体系放入冷却水中迅速降温至室温附近，同时将密闭容器内压力降低至常压；
反应体系温度降至常温常压后，将固态絮状产物与碱溶液进行分离，经0.01mol/L盐酸酸洗至PH＝4-5、经干燥，即得到Ti参与复合的主要由低结晶态纳米氢氧化Cr或纳米氧化Cr组成的复合纳米金属氧化物中间产物； 其形貌为胶絮状，且絮状微结构的粒径大小为0.5nm-25nm，由于初始合金中Ti含量相对Cr含量较少，含Ti中间产物未以钛酸盐或钛酸薄膜的方式出现，其主要通过原位嵌生复合的方式存在于低结晶态纳米氢氧化Cr或纳米氧化Cr中间产物中。
对比实施例1
按照Al 74Ti 21Nb 5(原子百分比)的配比称取金属Ti、Nb、Al原料，熔炼得到成分为Al 74Ti 21Nb 5的合金熔体，将该合金熔体凝固成铸锭，然后破碎成平均粒径约25μm的初始合金粉，其相组成主要由固溶有Nb元素的(NbTi)Al 3金属间化合物组成。
常压下，将0.5g上述制得的初始合金粉与50mL浓度为10mol/L，温度为25℃的NaOH水溶液混合反应2h，所得产物SEM形貌如图20所示。
可见，在该反应条件下，反应前后的原初始合金粉末的形状大致不变，仍然为原破碎状且具有棱角的粉末状颗粒，且其微观结构上也未有发生纳米碎化，也不生成大量分散分布的纳米氧化物粉末，而是生成纳米多孔网状结构构成的保留原棱角的粗大粉末颗粒，其粒度仍然与初始合金粉末的粒度相当，为数微米或数十微米级。因此，较低的温度下所发生的初始合金与碱溶液的反应与本发明在较高温度，尤其优选为沸点温度附近发生的反应完全不同，产物形貌也完全不同。
对比实施例2
本对比实施例提供一种纳米ZrO 2粉末的制备方法，包括如下步骤：
按照Al 75Zr 25(原子百分比)的名义配比称取金Al、Zr原料，熔炼得到成分主要为Al 75Zr 25的合金熔体，然后将该合金熔体凝固成合金锭，并将其破碎成平均粒径100μm的初始合金粉末，其凝固组织相组成主要由ZrAl 3金属间化合物组成。
常压下，将4g的Al 75Zr 25初始合金粉与NaOH水溶液反应，并不断搅拌；其中，NaOH溶液的浓度为12mol/L，温度为其常压下的沸点温度(～128℃)，NaOH溶液的体积为300ml；2min之内，析氢脱Al反应结束，得到几乎无色透明状的中间溶液。
析氢脱Al反应开始3min后，在剧烈搅拌状态下，将3000ml常温水在1min内缓慢加入所述反应体系中，使得碱溶液的浓度降低到2mol/L以下，同时碱溶液温度降低到40℃以下；在碱溶液浓度降低的过程中，原溶于碱溶液中的Zr元素以固态胶絮状氢氧化Zr的方式形核析出；
将固态絮状物质与中间溶液进行分离，并通过0.01mol/L的稀盐酸溶液中和清洗固态絮状物质吸附的残余碱至PH＝4-5，经干燥，即得到低结晶度的纳米氢氧化Zr，其TEM形貌照片及衍射谱如图21-22所示；可见，其主要为低结晶态，且形貌主要为胶絮状，絮状微结构的粒径大小为0.5nm-5nm。
将上述低结晶度的纳米氢氧化Zr在600℃下热处理2h，即得到明显晶化的纳米ZrO 2，其TEM形貌照片及衍射谱如图23-24所示；可见，图23显示更为清晰分层的衍射环，图24高倍TEM形貌下图22原来模糊的胶絮状形貌边界变成了清晰的白亮形貌边界。
将上述低结晶度的纳米氢氧化Zr在900℃下热处理2h，即得到晶态的纳米ZrO 2，其TEM形貌照片及衍射谱如图25-26所示；热处理后得到的晶态的纳米ZrO 2其虽然为多晶颗粒，但其烧结团聚成了实心的大颗粒，完全失去了颗粒的疏松性，也呈现低的比表面积。因此，这种结构难以通过后续球磨、砂磨过程进行碎化与细化。
以上所述实施例的各技术特征可以进行任意的组合，为使描述简洁，未对上述实施例中的各个技术特征所有可能的组合都进行描述，然而，只要这些技术特征的组合不存在矛盾，都应当认为是本说明书记载的范围。
以上所述实施例仅表达了本发明的几种实施方式，其描述较为具体和详细，但并不能因此而理解为对发明专利范围的限制。应当指出的是，对于本领域的普通技术人员来说，在不脱离本发明构思的前提下，还可以做出若干变形和改进，这些都属于本发明的保护范围。因此，本发明专利的保护范围应以所附权利要求为准。

Claims (15)

  1. 一种复合纳米金属氧化物的制备方法，其特征在于，包括如下步骤：
    步骤一，提供初始合金，所述初始合金的成分组成包含T类元素与A类元素，其中T类元素包含Al、Zn中的至少一种；A类元素包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；其中，M类子元素包含Cr、V、Nb、Ta、W、Mo、Mn、Y、La、Ce、Pr、Nd、Pm、Sm、Eu、Gd、Tb、Dy、Ho、Er、Tm、Yb、Lu中的至少一种；D类子元素包含Zr、Hf中的至少一种；所述初始合金的成分组成主要为A xT y，其中x，y为对应各类元素的原子百分比含量，且5≤x≤55％，45％≤y≤95％；所述初始合金的凝固组织主要由A-T金属间化合物组成；
    步骤二，将所述初始合金与碱溶液发生析氢脱T反应，通过控制碱溶液的温度T 1与浓度C 1，使反应过程中反应界面以不低于2μm/min的平均速率由初始合金表面向内推进；
    当初始合金中不含D类子元素时，初始合金与所述碱溶液通过析氢脱T反应发生纳米碎化，并经形状与成分重构生成形状在三维方向上至少有一维的尺度不超过500nm的含M与Ti的固态物质；
    当初始合金中含D类子元素时，初始合金与所述碱溶液通过析氢脱T反应发生纳米碎化，并经形状与成分重构生成形状在三维方向上至少有一维的尺度不超过500nm的含M或(与)Ti的固态物质；同时，D类子元素在高反应速率对应的碱浓度与温度情况下主要溶于所述碱溶液中，或在相对较低反应速率对应的碱浓度与温度情况下经形状与成分重构主要生成含D的固态物质；
    步骤三，析氢脱T反应结束后，
    当初始合金中不含D类子元素时，收集所述反应体系中的含M与Ti的固态物质，即得到含M与Ti的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；且所述含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；其中，含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含M中间产物与含Ti中间产物两者之间至少有一个是相；
    当初始合金中含D类子元素，且D类子元素主要以含D固态物质存在时，收集所述反应体系中的所有固态物质，即得到由含D中间产物与含M或(与)Ti中间产物组成的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；且含D中间产物、含M中间产物、含Ti中间产物之间彼此复合的方式包括原位嵌生复合；其中，含D中间产物、含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含D中间产物、含M中间产物、含Ti中间产物三者之间至少有一个是相；
    当初始合金中含D类子元素，且D类子元素主要溶于所述碱溶液中时，将液体加入步骤二所述反应体系中，使碱溶液的浓度降低至固态絮状氢氧化D可以析出的浓度C 2以下，析出的固态絮状氢氧化D与之前形成的含M或(与)Ti的固态物质混合，收集所有固态物质，即得到由纳米氢氧化D与含M或(与)Ti中间产物组成的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；其中，C 2<C 1，且当所述复合纳米金属氧化物中间产物中同时包括含M中间产物与含Ti中间产物时，含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；其中，含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含M中间产物与含Ti中间产物两者之间至少有一个是相；
    步骤四，将步骤三所述复合纳米金属氧化物中间产物进行热处理，即得到晶化程度提高的复合纳米金属氧化物；其包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；且Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相的尺度进行异类元素对应氧化物的复合。
  2. 一种复合纳米金属氧化物中间产物的制备方法，其特征在于，包括如下步骤：
    步骤1，提供初始合金，所述初始合金的成分组成包含T类元素与A类元素，其中T类元素包含Al、Zn中的至少一种；A类元素包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；其中，M类子元素包含Cr、V、Nb、Ta、W、Mo、Mn、Y、La、Ce、Pr、Nd、Pm、Sm、Eu、Gd、Tb、Dy、Ho、Er、Tm、Yb、Lu中的至少一种；D类子元素包含Zr、Hf中的至少一种；所述初始合金的成分组成主要为A xT y，其中x，y为对应各类元素的原子百分比含量，且5≤x≤55％，45％≤y≤95％；所述初始合金的凝固组织主要由A-T金属间化合物组成；
    步骤2，将所述初始合金与碱溶液发生析氢脱T反应，通过控制碱溶液的温度T 1与浓度C 1，使反应过程中反应界面以不低于2μm/min的平均速率由初始合金表面向内推进；
    当初始合金中不含D类子元素时，初始合金与所述碱溶液通过析氢脱T反应发生纳米碎化，并经形状与成分重构生成形状在三维方向上至少有一维的尺度不超过500nm的含M与Ti的固态物质；
    当初始合金中含D类子元素时，初始合金与所述碱溶液通过析氢脱T反应发生纳米碎化，并经形状与成分重构生成形状在三维方向上至少有一维的尺度不超过500nm的含M或(与)Ti的固态物质；同时，D类子元素在高反应速率对应的碱浓度与温度情况下主要溶于所述碱溶液中，或在相对较低反应速率对应的碱浓度与温度情况下经形状与成分重构主要生成含D的固态物质；
    步骤3，析氢脱T反应结束后，
    当初始合金中不含D类子元素时，收集所述反应体系中的含M与Ti的固态物质，即得到含M与Ti的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；且所述含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；其中，含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含M中间产物与含Ti中间产物两者之间至少有一个是相；
    当初始合金中含D类子元素，且D类子元素主要以含D固态物质存在时，收集所述反应体系中的所有固态物质，即得到由含D中间产物与含M或(与)Ti中间产物组成的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；且含D中间产物、含M中间产物、含Ti中间产物之间彼此复合的方式包括原位嵌生复合；其中，含D中间产物、含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含D中间产物、含M中间产物、含Ti中间产物三者之间至少有一个是相；
    当初始合金中含D类子元素，且D类子元素主要溶于所述碱溶液中时，将液体加入步骤二所述反应体系中，使碱溶液的浓度降低至固态絮状氢氧化D可以析出的浓度C 2以下，析出的固态絮状氢氧化D与之前形成的含M或(与)Ti的固态物质混合，收集所有固态物质，即得到由纳米氢氧化D与含M或(与)Ti中间产物组成的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；其中，C 2<C 1，且当所述复合纳米金属氧化物中间产物中同时包括含M中间产物与含Ti中间产物时，含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；其中，含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含M中间产物与含Ti中间产物两者之间至少有一个是相。
  3. 一种复合纳米金属氧化物的制备方法，其特征在于，包括如下步骤：
    步骤(1)，提供初始合金，所述初始合金的成分组成包含T类元素与A类元素，其中T类元素包含Al、Zn中的至少一种；A类元素包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；其中，M类子元素包含Cr、V、Nb、Ta、W、Mo、Mn、Y、La、Ce、Pr、Nd、Pm、Sm、Eu、Gd、Tb、Dy、Ho、Er、Tm、Yb、Lu中的至少一种；D类子元素包含Zr、Hf中的至少一种；所述初始合金的成分组成主要为A xT y，其中x，y为对应各类元素的原子百分比含量，且5≤x≤55％，45％≤y≤95％；所述初始合金的凝固组织主要由A-T金属间化合物组成；
    步骤(2)，将所述初始合金与温度为T 1，浓度为C 1的碱溶液混合；其中，T s溶液<T 1≤T f溶液，T f溶液为常压下所述参与反应的碱溶液的沸点温度；T s溶液为常压下所述参与反应的碱溶液的凝固点温度；
    步骤(3)，将步骤(2)所得的固态物质与浓度为C 2的碱溶液混合，然后将混合物置于密闭容器中，然后在高于常压的T 2温度处理一段时间，其中，T 2>T f溶液；
    步骤(4)，降温降压后，
    当初始合金中不含D类子元素时，收集反应体系内的固态物质，即得到含M与Ti的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；且所述含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；其中，含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含M中间产物与含Ti中间产物两者之间至少有一个是相；
    当初始合金中含D类子元素时，将液体加入降温降压后的反应体系中，使得稀释后的碱溶液浓度C 3<3mol/L，收集所有固态物质，即得到由含D固态物质与含M或(与)Ti的固态物质组成的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；其中，C 3<C 2，且当所述复合纳米金属氧化物中间产物中同时包括含M中间产物与含Ti中间产物时，含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；其中，含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含M中间产物与含Ti中间产物两者之间至少有一个是相；
    步骤(5)，将步骤(4)所述复合纳米金属氧化物中间产物进行热处理，即得到晶化程度提高的复合纳米金属氧化物；其包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；且Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相的尺度进行异类元素对应氧化物的复合。
  4. 一种复合纳米金属氧化物中间产物的制备方法，其特征在于，包括如下步骤：
    步骤1)，提供初始合金，所述初始合金的成分组成包含T类元素与A类元素，其中T类元素包含Al、Zn中的至少一种；A类元素包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；其中，M类子元素包含Cr、V、Nb、Ta、W、Mo、Mn、Y、La、Ce、Pr、Nd、Pm、Sm、Eu、Gd、Tb、Dy、Ho、Er、Tm、Yb、Lu中的至少一种；D类子元素包含Zr、Hf中的至少一种；所述初始合金的成分组成主要为A xT y，其中x，y为对应各类元素的原子百分比含量，且5≤x≤55％，45％≤y≤95％；所述初始合金的凝固组织主要由A-T金属间化合物组成；
    步骤2)，将所述初始合金与温度为T 1，浓度为C 1的碱溶液混合；其中，T s溶液<T 1≤T f溶液，T f溶液为常压下所述参与反应的碱溶液的沸点温度；T s溶液为常压下所述参与反应的碱溶液的凝固点温度；
    步骤3)，将步骤2)所得的固态物质与浓度为C 2的碱溶液混合，然后将混合物置于密闭容器中，然后在高于常压的T 2温度处理一段时间，其中，T 2>T f溶液；
    步骤4)，降温降压后，
    当初始合金中不含D类子元素时，收集反应体系内的固态物质，即得到含M与Ti的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；且所述含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；其中，含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含M中间产物与含Ti中间产物两者之间至少有一个是相；
    当初始合金中含D类子元素时，将液体加入降温降压后的反应体系中，使得稀释后的碱溶液浓度C 3<3mol/L，收集所有固态物质，即得到由含D固态物质与含M或(与)Ti的固态物质组成的复合纳米金属氧化物中间产物，其形状在三维方向上至少有一维的尺度不超过500nm；其中，C 3<C 2；且当所述复合纳米金属氧化物中间产物中同时包括含M中间产物与含Ti中间产物时，含M中间产物与含Ti中间产物复合的方式包括原位嵌生复合；其中，含M中间产物、含Ti中间产物可以是对应的原子或原子团簇，也可以是对应的相，且含M中间产物与含Ti中间产物两者之间至少有一个是相。
  5. 一种复合纳米金属氧化物，其特征在于，根据权利要求1所述制备方法制备，其制备过程及详细特征见权利要求1所述，其详细特征还包括：
    所述复合纳米金属氧化物中，包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；且所述复合纳米金属氧化物中，Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相的尺度进行异类元素对应氧化物的复合；其中，所述原子/原子团簇尺度大小为0.25nm-2.5nm；所述细相的平均粒径低于250nm；其中，M类子元素包含Cr、V、Nb、Ta、W、Mo、Mn、Y、La、Ce、Pr、Nd、Pm、Sm、Eu、Gd、Tb、Dy、Ho、Er、Tm、Yb、Lu中的至少一种；D类子元素包含Zr、Hf中的至少一种。
  6. 根据权利要求5所述的复合纳米金属氧化物，其特征在于，所述复合纳米金属氧化物的颗粒疏松性或(与)比表面积高于相似工艺制备的对应的单一纳米金属氧化物的颗粒疏松性或(与)比表面积。
  7. 一种复合纳米金属氧化物中间产物，其特征在于，根据权利要求2所述制备方法制备，其制备过程及详细特征见权利要求2所述，其详细特征还包括：
    所述复合纳米金属氧化物中间产物中，包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；且所述复合纳米金属氧化物中间产物中，Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相的尺度进行异类元素对应氧化物中间产物的复合；其中，所述原子/原子团簇尺度大小为0.25nm-2.5nm；所述细相的平均粒径低于250nm；其中，M类子元素包含Cr、V、Nb、Ta、W、Mo、Mn、Y、La、Ce、Pr、Nd、Pm、Sm、Eu、Gd、Tb、Dy、Ho、Er、Tm、Yb、Lu中的至少一种；D类子元素包含Zr、Hf中的至少一种。
  8. 根据权利要求7所述的复合纳米金属氧化物中间产物，其特征在于，所述复合纳米金属氧化物中间产物的热稳定性或(与)晶化温度高于相似工艺制备的对应的单一纳米金属氧化物中间产物的热稳定性或(与)晶化温度。
  9. 一种复合纳米金属氧化物，其特征在于，根据权利要求3所述制备方法制备，其制备过程及详细特征见权利要求3所述，其详细特征还包括：
    所述复合纳米金属氧化物中，包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；且所述复合纳米金属氧化物中，Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相的尺度进行异类元素对应氧化物的复合；其中，所述原子/原子团簇尺度大小为0.25nm-2.5nm；所述细相的平均粒径低于250nm；其中，M类子元素包含Cr、V、Nb、Ta、W、Mo、Mn、Y、La、Ce、Pr、Nd、Pm、Sm、Eu、Gd、Tb、Dy、Ho、Er、Tm、Yb、Lu中的至少一种；D类子元素包含Zr、Hf中的至少一种。
  10. 根据权利要求9所述的复合纳米金属氧化物，其特征在于，所述复合纳米金属氧化物的颗粒疏松性或(与)比表面积高于相似工艺制备的对应的单一纳米金属氧化物的颗粒疏松性或(与)比表面积。
  11. 一种复合纳米金属氧化物中间产物，其特征在于，根据权利要求4所述制备方法制备，其制备过程及详细特征见权利要求4所述，其详细特征还包括：
    所述复合纳米金属氧化物中间产物中，包含元素Ti、M类子元素、D类子元素这三类子元素中的至少两类；且所述复合纳米金属氧化物中间产物中，Ti元素、M类子元素、D类子元素这三类子元素中至少有两类子元素在原子/原子团簇尺度或细相的尺度进行异类元素对应氧化物中间产物的复合；其中，所述原子/原子团簇尺度大小为0.25nm-2.5nm；所述细相的平均粒径低于250nm；其中，M类子元素包含Cr、V、Nb、Ta、W、Mo、Mn、Y、La、Ce、Pr、Nd、Pm、Sm、Eu、Gd、Tb、Dy、Ho、Er、Tm、Yb、Lu中的至少一种；D类子元素包含Zr、Hf中的至少一种。
  12. 根据权利要求11所述的复合纳米金属氧化物中间产物，其特征在于，所述复合纳米金属氧化物中间产物的热稳定性或(与)晶化温度高于相似工艺制备的对应的单一纳米金属氧化物中间产物的热稳定性或(与)晶化温度。
  13. 根据权利要求1-4任一项所述制备方法制备的产物材料，或权利要求5-12所述材料，在复合材料、催化材料、陶瓷材料、耐火材料、先进电子材料、电池材料、变色材料、吸波材料、污水降解材料、杀菌材料、涂料、颜料、热喷涂材料、传感器中的应用。
  14. 一种复合氧化物陶瓷的制备方法，其特征在于，包括如下步骤：
    步骤S1，制备混合均匀且细化的混合粉料，所述混合粉料的组成包括权利要求1-4任一项所述制备方法制备的复合纳米金属氧化物或中间产物，以及外加粉体；其中，所述复合纳米金属氧化物或中间产物在混合粉料中的摩尔百分比含量为V 1，外加粉体在混合粉料中的摩尔百分比含量为V 2，且所述外加粉体包含Al 2O 3、CaO、MgO、SiO 2、B 2O 3、BeO中的至少一种，1％≤V 1≤100％，0≤V 2≤99％；
    步骤S2，将混合粉料压制成为坯体，经高温焙烧，即制得复合氧化物陶瓷材料。
  15. 一种复合氧化物陶瓷，其特征在于，根据权利要求14所述制备方法制备，其详细特征见权利要求14所述。
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