Powder alloy for preparing automobile gear and preparation method of powder alloy

Abstract

The invention discloses a powder alloy for preparing an automobile gear and a preparation method of the powder alloy, belongs to the technical field of alloy material preparation, and aims at solving the problem that in the prior art, the forming capacity and the stacking performance of the powder alloy for preparing the automobile gear still need to be further improved. According to the invention, zirconium-based six-element framework composite powder, aluminum-titanium-niobium reinforced composite powder and cerium-yttrium-zirconium-molybdenum interface modified composite powder are constructed and are synergistically introduced into a multi-element alloy-based powder system, so that composite design is realized from three aspects of framework support, reinforced structure construction and interface transition adjustment; and therefore, the powder accumulation and pressing forming state can be improved, and the structure continuity, the densification coordination and the service stability of automobile gear workpieces are improved.

Description

Technical Field

[0001] This invention relates to the field of alloy material preparation technology, specifically to a powder alloy for automotive gear manufacturing and its preparation method. Background Technology

[0002] Currently, powder alloys for automotive gears are mostly prepared using powder metallurgy processes. Common raw materials include iron-based pre-alloyed powders, diffusion alloy powders, or mechanically mixed powders, which are combined with alloying components such as nickel, copper, molybdenum, chromium, and manganese, as well as lubricants. Gear parts are formed through processes such as mixing, pressing, sintering, and shaping. In order to balance the strength, dimensional accuracy, and mass production requirements of the parts, existing technologies often optimize the powder alloys used for automotive gear preparation by adjusting the powder particle size distribution, particle morphology, the method of introducing alloying elements, and the form of adding sintering aids, reinforcing phases, and surface modifying components.

[0003] However, existing powder alloys for automotive gear manufacturing still generally suffer from insufficient mold adaptability at the powder end. Specifically, there are often differences in particle size, density, surface condition, and particle morphology between different components. After mixing, uneven dispersion, local agglomeration, and secondary segregation during transportation are likely to occur, which affects the uniformity of mold loading and filling stability during pressing. Especially in multi-component systems, if there is a lack of good synergistic packing relationship between particles, it is easy to cause inconsistent density distribution after the powder flows into the mold cavity, making it difficult to obtain a stable molding state for the corners, teeth, and local complex structural areas of the compact.

[0004] Furthermore, while some powder alloys in the existing technology incorporate reinforcing components, composite additives, or surface-modifying components, they may also lead to a decline in powder packing performance while improving the material's microstructure and properties. For example, some added components can complicate the surface state of particles, increasing interparticle friction and jamming, and reducing the powder's rearrangement ability in the mold. Insufficient interfacial bonding between some composite components and the matrix powder may also lead to increased porosity and inconsistent local densification during the pressing process. Therefore, there is still room for further optimization in terms of packing performance and forming capability of existing powder alloys for automotive gear manufacturing.

[0005] To address this technical deficiency, a solution is proposed. Summary of the Invention

[0006] The purpose of this invention is to provide a powder alloy for manufacturing automotive gears and its preparation method, which addresses the problem that the forming ability and deposition performance of powder alloys for manufacturing automotive gears in the prior art still need to be further improved.

[0007] The objective of this invention can be achieved through the following technical solutions:

[0008] A powder alloy for manufacturing automotive gears comprises the following raw materials in parts by weight: 78-82 parts zirconium-based hexa-elemental framework composite powder, 14-20 parts aluminum-titanium-niobium reinforced composite powder, and 5-9 parts cerium-yttrium-zirconium-molybdenum interface modified composite powder.

[0009] The preparation method of the zirconium-based six-membered framework composite powder is as follows: a six-membered metal fluorine-containing precursor, zirconium oxychloride octahydrate, anhydrous sodium acetate, ethylene glycol and deionized water are added to a reaction vessel and stirred. After mixing evenly, the reaction vessel is heated to 75-85℃ and stirred for 30-60 minutes. Then, the coordination component is added, and the temperature is further increased to 105-115℃ and stirred for 2-3 hours. The zirconium-based six-membered framework composite powder is obtained after post-treatment.

[0010] Furthermore, in the preparation of zirconium-based six-membered framework composite powder, the ratio of the hexa-metal fluorine-containing precursor, zirconium oxychloride octahydrate, anhydrous sodium acetate, ethylene glycol, deionized water, and coordinating component is 16-20g:5-7g:4-5g:100mL:50mL:4-6mL, wherein the coordinating component is an 80wt% hydrazine aqueous solution. The post-treatment includes: after the reaction is completed, filtering to collect the filter cake and drying it to obtain zirconium-based six-membered framework composite powder.

[0011] Furthermore, the preparation method of the hexa-metal fluorine-containing precursor is as follows: add multi-metal hydrate, ethylene glycol and deionized water into a reaction vessel and stir. After mixing evenly, add ammonium fluoride and citric acid, then heat the reaction vessel to 58-65℃ and stir for 40-60 min. Then continue to heat to 75-85℃ and stir for 2-3 h. After the reaction is completed, filter, collect the filter cake and dry it to obtain the hexa-metal fluorine-containing precursor.

[0012] Furthermore, in the preparation of the hexa-metal fluorine-containing precursor, the ratio of the multi-metal hydrate, ethylene glycol, deionized water, ammonium fluoride, and citric acid is 28-38g:120mL:80mL:2-3g:5-7g. The multi-metal hydrate is obtained by mixing ferric chloride hexahydrate, nickel chloride hexahydrate, cobalt chloride hexahydrate, chromium nitrate nonahydrate, ammonium heptamolybdate tetrahydrate, and niobium pentachloride in a ratio of 7-9g:6-8g:4-6g:5-7g:4-5g:2-3g.

[0013] Furthermore, the aluminum-titanium-niobium reinforced composite powder is prepared by the following method:

[0014] A1. Add anhydrous ethanol and deionized water to the reactor and stir. Then add aluminum nitrate nonahydrate and niobium pentachloride. After mixing evenly, add isopropyl titanate, then add peroxide component and triethyl phosphate. Stir the reactor at 5-10℃ for 40-60 min. Then raise the temperature to 35-40℃ and stir for 60-80 min. Then raise the temperature to 60-70℃ and stir for 1-2 h. The post-processing yields aluminum-titanium-niobium reinforced precursor.

[0015] A2. Add the aluminum-titanium-niobium reinforced precursor, diethylenetriamine and formamide to the reaction vessel and stir. After mixing evenly, heat the reaction vessel to 90-95℃ and stir for 1-2 hours. Then continue to heat to 125-135℃ and stir for 40-60 minutes. After the reaction is completed, distill under reduced pressure until no liquid is collected to obtain aluminum-titanium-niobium reinforced composite powder.

[0016] Further, in step A1, the ratio of anhydrous ethanol, deionized water, aluminum nitrate nonahydrate, niobium pentachloride, isopropyl titanate, peroxide component, and triethyl phosphate is 120mL:30mL:4-5g:1-2g:4-5mL:4-5mL:5-6mL, wherein the peroxide component is a 30wt% aqueous solution of hydrogen peroxide. The post-treatment includes: after the reaction is completed, vacuum distillation until no liquid is collected, followed by milling through a 120-mesh sieve to obtain the aluminum-titanium-niobium reinforced precursor.

[0017] Furthermore, in step A2, the ratio of the aluminum-titanium-niobium reinforced precursor, diethylenetriamine, and formamide is 14-18g:7-9mL:70-90mL.

[0018] Furthermore, the preparation method of the cerium-yttrium-zirconium-molybdenum interface-modified composite powder is as follows: sodium molybdate dihydrate and deionized water are added to a reaction vessel and stirred. After mixing evenly, 30wt% hydrogen peroxide aqueous solution is added. The reaction vessel is stirred for 12-30 minutes at 8-12℃. Then, a metal salt solution is added and mixed evenly. The temperature is raised to 35-45℃, and sodium bicarbonate is added. The temperature is then raised to 60-70℃ and stirred for 1-2 hours. After the reaction is completed, the filter cake is collected, dried, and passed through a 120-mesh sieve to obtain the cerium-yttrium-zirconium-molybdenum interface-modified composite powder.

[0019] Furthermore, in the preparation of the cerium-yttrium-zirconium-molybdenum interface-modified composite powder, the ratio of sodium molybdate dihydrate, deionized water, 30wt% hydrogen peroxide aqueous solution, metal salt solution, and sodium bicarbonate is 4-5g:120mL:7-9mL:100mL:6-8g. The metal salt solution is obtained by mixing cerium nitrate hexahydrate, yttrium nitrate hexahydrate, zirconium oxychloride octahydrate, and deionized water in a ratio of 2.5-3.5g:0.8-1.2g:4.5-5.5g:100mL.

[0020] This invention also discloses a method for preparing powder alloys for automotive gear manufacturing, comprising the following steps:

[0021] S1. Weigh out the following by weight: zirconium-based six-element framework composite powder, aluminum-titanium-niobium reinforced composite powder and cerium-yttrium-zirconium-molybdenum interface modified composite powder, add them to a mixer and mix them. After mixing evenly, grind them through an 80-120 mesh sieve to obtain composite substrate mixed powder.

[0022] S2. The composite substrate mixed powder is placed in a corundum boat and then transferred to a tube furnace. Under vacuum conditions, the temperature is raised to 380-430℃ and held for 40-60 minutes. Then, mixed gas is introduced and the temperature is raised to 880-960℃ and held for 1-2 hours. Then, the temperature is raised to 1080-1140℃ under vacuum conditions and held for 40-60 minutes. The post-processing yields multi-element alloy base powder.

[0023] Furthermore, in step S2, the vacuum degree of the vacuum condition is -0.098MPa. The mixed gas is obtained by mixing hydrogen and argon in a volume ratio of 1:6-10. The post-processing includes: cooling to 150-250℃ after heat preservation and removing from the furnace, crushing the material and then mechanically pulverizing it, then passing it through a 200-320 mesh sieve, collecting the sieve material, and obtaining multi-element alloy-based powder.

[0024] The present invention has the following beneficial effects:

[0025] 1. When the zirconium-based six-element framework composite powder prepared by this invention is placed in the main body proportion of the composite substrate system, the powder gradation relationship and particle support framework tend to stabilize. During the filling process, particles of different sizes are more likely to form continuous spatial interlocking, and particle rearrangement is also more sufficient under vibration conditions. As a result, the powder exhibits a relatively compact packing characteristic in both loose and vibrated states. This packing state is not formed independently by a single framework component. After being combined with aluminum-titanium-niobium reinforced composite powder, the compensation of the gaps between the fine particles is more sufficient. In addition, combined with the adjustment of the particle surface contact state by the cerium-yttrium-zirconium-molybdenum interface modified composite powder, local bridging, segregation and density fluctuations are suppressed during the filling process, and the density distribution inside the compact is more balanced. Thus, the material configuration shows good packing adaptability in the powder stage and retains a more stable structural foundation for the subsequent forming process.

[0026] 2. After the aluminum-titanium-niobium reinforced composite powder prepared in this invention is introduced, the shrinkage path formed by the composite substrate during heat treatment and sintering is more continuous, and the densification process in local areas is less prone to significant mismatch. The expansion of the sintering neck and the closing of pores can be carried out in a more coordinated state, and the tendency to retain the open pores inside the gear blank is correspondingly weakened. This structural evolution does not depend solely on the reinforcing component itself. After being combined with the zirconium-based six-element framework composite powder, a good matching relationship is maintained between the framework support and volume shrinkage during sintering. In addition, combined with the continuity effect of the cerium-yttrium-zirconium-molybdenum interface modified composite powder on the contact boundary of multiple components, the microstructure connection between different regions is smoother, and the degree of pore connectivity is reduced. Based on the above structural configuration, the sintered body maintains a stable forming profile while the internal microstructure tends to be complete, and the structural state corresponding to the porosity is more suitable for subsequent service load conditions.

[0027] 3. When the cerium-yttrium-zirconium-molybdenum interface-modified composite powder prepared in this invention is incorporated into the system, the stress transmission path near the surface of the gear tooth and at the local structural boundary becomes more continuous under repeated contact loads. The local loads that were originally prone to accumulate in the interface transition zone are dispersed, and the weak points on which pitting corrosion initiation depends are less likely to appear prematurely. As a result, the damage propagation process of the single tooth load area is more moderate. This service state is not determined by the interface modification component alone. When it is combined with the aluminum-titanium-niobium reinforced composite powder, the stability of the tooth surface load-bearing layer is more easily maintained. Furthermore, with the relatively uniform pressing foundation and more coordinated sintering structure provided by the aforementioned zirconium-based six-element framework composite powder as support, the stress distribution between adjacent tooth surfaces during meshing becomes more consistent. Thus, the material system forms a continuous connection between the local contact state of a single tooth and the overall meshing state of the gear pair, keeping the service damage tendency reflected by the pitting corrosion area ratio within a relatively mild range. Attached Figure Description

[0028] To more clearly illustrate the technical solutions in the embodiments of the present invention or the prior art, the drawings used in the description of the embodiments or the prior art will be briefly introduced below. Obviously, the drawings described below are only some embodiments of the present invention. For those skilled in the art, other drawings can be obtained based on these drawings without creative effort.

[0029] Figure 1 SEM image of the zirconium-based six-membered framework composite powder prepared in Example 3;

[0030] Figure 2 SEM image of the aluminum-titanium-niobium reinforced composite powder prepared in Example 6;

[0031] Figure 3 The image shows a SEM image of the cerium-yttrium-zirconium-molybdenum interface-modified composite powder prepared in Example 9. Detailed Implementation

[0032] The technical solution of the present invention will be clearly and completely described below with reference to the embodiments. Obviously, the described embodiments are only some embodiments of the present invention, and not all embodiments. Based on the embodiments of the present invention, all other embodiments obtained by those skilled in the art without creative effort are within the scope of protection of the present invention.

[0033] Example 1

[0034] This embodiment provides a method for preparing zirconium-based six-membered framework composite powder, including the following steps:

[0035] Step I: Preparation of a hexa-metal fluorine-containing precursor

[0036] Weigh out 7.0g of ferric chloride hexahydrate, 6.0g of nickel chloride hexahydrate, 4.0g of cobalt chloride hexahydrate, 5.0g of chromium nitrate nonahydrate, 4.0g of ammonium heptamolybdate tetrahydrate and 2.0g of niobium pentachloride and mix them to obtain a multi-metal salt hydrate;

[0037] Weigh out 28.0 g of multi-metal hydrate, 120.0 mL of ethylene glycol and 80.0 mL of deionized water and add them to the reaction vessel. Stir and mix well. Then add 2.0 g of ammonium fluoride and 5.0 g of citric acid. Heat the reaction vessel to 58 °C and stir for 40 min. Then continue to heat to 75 °C and stir for 2 h. After the reaction is complete, filter, collect the filter cake and dry it to obtain the hexa-metal fluorine-containing precursor.

[0038] Step II: Preparation of zirconium-based six-membered framework composite powder

[0039] Weigh out 16.0g of a hexa-metal fluorine-containing precursor, 5.0g of zirconium oxychloride octahydrate, 4.0g of anhydrous sodium acetate, 100.0mL of ethylene glycol, and 50.0mL of deionized water and add them to a reaction vessel. Stir until the mixture is homogeneous, then heat the reaction vessel to 75℃ and stir for 30min. Add 4mL of 80wt% hydrazine aqueous solution, then continue to heat to 105℃ and stir for 2h. After the reaction is complete, filter to collect the filter cake and dry it to obtain zirconium-based hexa-framework composite powder.

[0040] The reaction principle for preparing zirconium-based six-membered framework composite powder is as follows:

[0041] In the ethylene glycol-water system, metal ions such as Fe, Ni, Co, Cr, Mo, and Nb first coordinate with citric acid and solvent molecules. The introduction of fluoride ions alters the local coordination environment and forms relatively stable fluorine-containing complex structures with some metal centers. Under continuous heating, dehydration condensation and hydroxylation aggregation gradually occur within the system, generating a relatively homogeneous six-membered metal fluorine-containing precursor. Subsequently, zirconium oxychloride is added, and ZrO... 2+The relevant species undergo hydrolysis and condensation in a medium regulated by sodium acetate and hydrazine, and combine with the metal-oxygen coordination units in the precursor through adsorption, coordination exchange and heterogeneous deposition, ultimately forming a six-component composite powder with zirconium component.

[0042] The working principle of zirconium-based hexa-elemental framework composite powder in multi-element alloy-based powder is as follows:

[0043] In this process, the six-membered fluorine-containing metal precursor and the zirconium-based six-membered framework composite powder formed in steps I and II essentially correspond to the pre-organized structure source and the subsequent spatial framework structure source of the multi-component metal components, respectively. The former establishes a relatively continuous distribution relationship for components such as Fe, Ni, Co, Cr, Mo, and Nb at the particle scale, reducing the tendency for local segregation and compositional dispersion in the final multi-component alloy-based powder. The latter further introduces zirconium-based framework units with supporting and boundary stabilizing effects, thereby enhancing the intergranular bonding, constraint, and subsequent structural integration capabilities. Meanwhile, ammonium fluoride, citric acid, zirconium oxychloride, sodium acetate, hydrazine, and ethylene glycol-water medium participate in the construction of this composite system from aspects such as local structural adjustment, unified organization of multiple components, introduction of skeleton components, optimization of boundary distribution, enhanced interfacial bonding, and maintenance of particle uniformity. The combined effect of these factors makes the final multi-element alloy-based powder exhibit a more coordinated evolution trend in terms of compositional uniformity, particle packing, compaction response, and sintering structure continuity. Furthermore, it forms a more continuous structural transfer basis for controlling the porosity of automotive gears and suppressing pitting damage under service conditions.

[0044] Example 2

[0045] This embodiment provides a method for preparing zirconium-based six-membered framework composite powder, including the following steps:

[0046] Step I: Preparation of a hexa-metal fluorine-containing precursor

[0047] Weigh out 9.0g of ferric chloride hexahydrate, 8.0g of nickel chloride hexahydrate, 6.0g of cobalt chloride hexahydrate, 7.0g of chromium nitrate nonahydrate, 5.0g of ammonium heptamolybdate tetrahydrate, and 3.0g of niobium pentachloride and mix them to obtain a multi-metal salt hydrate;

[0048] Weigh out 38.0 g of multi-metal hydrate, 120.0 mL of ethylene glycol and 80.0 mL of deionized water and add them to the reaction vessel. Stir and mix well. Then add 3.0 g of ammonium fluoride and 7.0 g of citric acid. Heat the reaction vessel to 65 °C and stir for 60 min. Then continue to heat to 85 °C and stir for 3 h. After the reaction is complete, filter, collect the filter cake and dry it to obtain the hexa-metal fluorine-containing precursor.

[0049] Step II: Preparation of zirconium-based six-membered framework composite powder

[0050] Weigh out 20.0g of a hexa-metal fluorine-containing precursor, 7.0g of zirconium oxychloride octahydrate, 5.0g of anhydrous sodium acetate, 100.0mL of ethylene glycol, and 50.0mL of deionized water and add them to a reaction vessel. Stir until the mixture is homogeneous, then heat the reaction vessel to 85℃ and stir for 60min. Add 6mL of 80wt% hydrazine aqueous solution, then continue to heat to 115℃ and stir for 3h. After the reaction is complete, filter to collect the filter cake and dry it to obtain zirconium-based hexa-framework composite powder.

[0051] Example 3

[0052] This embodiment provides a method for preparing zirconium-based six-membered framework composite powder, including the following steps:

[0053] Step I: Preparation of a hexa-metal fluorine-containing precursor

[0054] Weigh out 8.0g of ferric chloride hexahydrate, 7.0g of nickel chloride hexahydrate, 5.0g of cobalt chloride hexahydrate, 6.0g of chromium nitrate nonahydrate, 4.5g of ammonium heptamolybdate tetrahydrate, and 2.5g of niobium pentachloride and mix them to obtain a multi-metal salt hydrate;

[0055] Weigh out 32.0 g of multi-metal hydrate, 120.0 mL of ethylene glycol and 80.0 mL of deionized water and add them to the reaction vessel. Stir and mix well. Then add 2.5 g of ammonium fluoride and 6.0 g of citric acid. Heat the reaction vessel to 60 °C and keep it at that temperature for 50 min. Then continue to heat it to 80 °C and keep it at that temperature for 3 h. After the reaction is complete, filter and collect the filter cake and dry it to obtain the six-membered metal fluorine precursor.

[0056] Step II: Preparation of zirconium-based six-membered framework composite powder

[0057] Weigh out 18.0g of a hexa-metal fluorine-containing precursor, 6.0g of zirconium oxychloride octahydrate, 4.5g of anhydrous sodium acetate, 100.0mL of ethylene glycol, and 50.0mL of deionized water and add them to a reaction vessel. Stir until the mixture is homogeneous, then heat the reaction vessel to 80℃ and stir for 45min. Add 5mL of 80wt% hydrazine aqueous solution, then continue to heat to 110℃ and stir for 3h. After the reaction is complete, filter to collect the filter cake and dry it to obtain zirconium-based hexa-framework composite powder.

[0058] Example 4

[0059] This embodiment provides a method for preparing aluminum-titanium-niobium reinforced composite powder, including the following steps:

[0060] Step ①: Preparation of aluminum-titanium-niobium reinforced precursor

[0061] Weigh out 120.0 mL of anhydrous ethanol and 30.0 mL of deionized water and add them to the reaction vessel and stir. Then add 4.0 g of aluminum nitrate nonahydrate and 1.0 g of niobium pentachloride, mix well, add 4.0 mL of isopropyl titanate, then add 4.0 mL of 30 wt% hydrogen peroxide aqueous solution and 5.0 mL of triethyl phosphate. Stir the reaction vessel at 5 °C for 40 min, then raise the temperature to 35 °C and stir for 60 min, then raise the temperature to 60 °C and stir for 1 h. After the reaction is completed, distill under reduced pressure until no liquid is collected, then grind through a 120 mesh sieve to obtain the aluminum-titanium-niobium reinforced precursor.

[0062] Step 2: Preparation of aluminum-titanium-niobium reinforced composite powder

[0063] Weigh out 14.0g of aluminum-titanium-niobium reinforced precursor, 7.0mL of diethylenetriamine and 70.0mL of formamide and add them to the reaction vessel. Stir and mix evenly. Then heat the reaction vessel to 90℃ and keep it at that temperature for 1h. Then continue to heat to 125℃ and keep it at that temperature for 40min. After the reaction is completed, distill under reduced pressure until no liquid is collected to obtain aluminum-titanium-niobium reinforced composite powder.

[0064] The reaction principle for preparing aluminum-titanium-niobium reinforced precursors is as follows:

[0065] In an ethanol-water mixed medium, aluminum and niobium precursor salts first undergo solvation dispersion. Subsequently, isopropyl titanate gradually hydrolyzes in the aqueous system to form hydroxyl-containing titanium coordination species. The addition of hydrogen peroxide stabilizes some titanium and niobium centers in a peroxy coordination form and modulates the local coordination environment. Simultaneously, triethyl phosphate participates in coordination and esterification under reaction conditions, gradually forming Al-O, Ti-O, Nb-O, and PO-related multi-metal oxygen-containing coordination units in the system. As the temperature increases, hydroxyl condensation, oxygen bridging, and complex rearrangement further occur between different metal centers, and the system gradually transforms from a dispersed complex into a more homogeneous multi-metal complex precursor. After removing volatile components, a precursor powder with aluminum, titanium, and niobium as the main components and containing phosphorus-oxygen coordination structures is obtained.

[0066] The working principle of aluminum-titanium-niobium reinforced composite powder in multi-element alloy-based powders is as follows:

[0067] In this process, the aluminum-titanium-niobium reinforced precursor and aluminum-titanium-niobium reinforced composite powder obtained in steps ① and ② essentially correspond to the pre-organized structural source and the subsequent stabilization source of the reinforcing components, respectively. The former enables Al, Ti, Nb, and phosphorus-containing oxygen structural units to form a relatively continuous proximity distribution at the particle scale, providing a foundation for the uniform introduction, diffusion synergy, and formation of local load-bearing units of the reinforcing components in the final multi-element alloy-based powder, reducing the tendency for the reinforcing source to be dispersed, locally enriched, or structurally fragmented. The latter, based on the precursor, further endows the system with a more stable composite reinforcing characteristic, improving the distribution state, boundary connections, and subsequent microstructure integration of the reinforcing components within the powder. The structure becomes more continuous; meanwhile, aluminum nitrate, niobium pentachloride, and isopropyl titanate provide the sources of aluminum, niobium, and titanium reinforcement structures, respectively. Hydrogen peroxide and triethyl phosphate mainly participate in the local coordination environment and the construction of phosphorus-containing oxygen structural units. Diethylenetriamine and formamide are more reflected in the regulation of the boundary state, particle uniformity, and internal connection integrity of the composite reinforcement structure. The combined effect of the above factors makes the final multi-element alloy-based powder exhibit a more coordinated evolution trend in terms of the distribution of reinforcement components, the continuity of the internal structure of particles, the compaction response, and the integrity of the load-bearing structure after sintering. Furthermore, it forms a more stable reinforcement structure basis for controlling the porosity of automotive gears and suppressing pitting damage under service conditions.

[0068] Example 5

[0069] This embodiment provides a method for preparing aluminum-titanium-niobium reinforced composite powder, including the following steps:

[0070] Step ①: Preparation of aluminum-titanium-niobium reinforced precursor

[0071] Weigh out 120.0 mL of anhydrous ethanol and 30.0 mL of deionized water and add them to the reaction vessel and stir. Then add 5.0 g of aluminum nitrate nonahydrate and 2.0 g of niobium pentachloride, mix well, add 5.0 mL of isopropyl titanate, then add 5.0 mL of 30 wt% hydrogen peroxide aqueous solution and 6.0 mL of triethyl phosphate. Stir the reaction vessel at 10 °C for 60 min, then raise the temperature to 40 °C and stir for 80 min, then raise the temperature to 70 °C and stir for 2 h. After the reaction is completed, distill under reduced pressure until no liquid is collected, then grind through a 120 mesh sieve to obtain the aluminum-titanium-niobium reinforced precursor.

[0072] Step 2: Preparation of aluminum-titanium-niobium reinforced composite powder

[0073] Weigh out 18.0g of aluminum-titanium-niobium reinforced precursor, 9.0mL of diethylenetriamine and 90.0mL of formamide and add them to the reaction vessel. Stir and mix evenly. Then heat the reaction vessel to 95℃ and keep it at that temperature for 2 hours. Then continue to heat to 135℃ and keep it at that temperature for 60 minutes. After the reaction is completed, distill under reduced pressure until no liquid is collected to obtain aluminum-titanium-niobium reinforced composite powder.

[0074] Example 6

[0075] This embodiment provides a method for preparing aluminum-titanium-niobium reinforced composite powder, including the following steps:

[0076] Step ①: Preparation of aluminum-titanium-niobium reinforced precursor

[0077] Weigh out 120.0 mL of anhydrous ethanol and 30.0 mL of deionized water and add them to the reaction vessel and stir. Then add 4.5 g of aluminum nitrate nonahydrate and 1.5 g of niobium pentachloride, mix well, add 4.5 mL of isopropyl titanate, then add 4.5 mL of 30 wt% hydrogen peroxide aqueous solution and 5.5 mL of triethyl phosphate. Stir the reaction vessel at 8 °C for 50 min, then raise the temperature to 40 °C and stir for 70 min, then raise the temperature to 65 °C and stir for 2 h. After the reaction is completed, distill under reduced pressure until no liquid is collected, then grind through a 120 mesh sieve to obtain the aluminum-titanium-niobium reinforced precursor.

[0078] Step 2: Preparation of aluminum-titanium-niobium reinforced composite powder

[0079] Weigh out 16.0g of aluminum-titanium-niobium reinforced precursor, 8.0mL of diethylenetriamine and 80.0mL of formamide and add them to the reaction vessel. Stir and mix evenly. Then heat the reaction vessel to 95℃ and keep it at that temperature for 2 hours. Then continue to heat to 130℃ and keep it at that temperature for 50 minutes. After the reaction is completed, distill under reduced pressure until no liquid is collected to obtain aluminum-titanium-niobium reinforced composite powder.

[0080] Example 7

[0081] This embodiment provides a method for preparing powder alloy for automotive gear manufacturing, including the following steps:

[0082] Step 1: Preparation of cerium-yttrium-zirconium-molybdenum interface-modified composite powder

[0083] Weigh out 2.5g of cerium nitrate hexahydrate, 0.8g of yttrium nitrate hexahydrate, and 4.5g of zirconium oxychloride octahydrate, and mix them with 100.0mL of deionized water to obtain a metal salt solution;

[0084] Weigh 4.0 g of sodium molybdate dihydrate and 120.0 mL of deionized water and add them to the reaction vessel. Stir and mix well. Then add 7.0 mL of 30 wt% hydrogen peroxide aqueous solution. Stir the reaction vessel at 8 °C for 12 min. Then add 100.0 mL of metal salt solution and mix well. Raise the temperature to 35 °C and add 6.0 g of sodium bicarbonate. Continue to raise the temperature to 60 °C and keep stirring for 1 h. After the reaction is complete, filter and collect the filter cake. Dry the cake and pass it through a 120 mesh sieve to obtain cerium-yttrium-zirconium-molybdenum interface modified composite powder.

[0085] The reaction principle for preparing cerium-yttrium-zirconium-molybdenum interface-modified composite powder is as follows:

[0086] Under low-temperature aqueous conditions, molybdate and hydrogen peroxide first form relatively stable peroxymolybdenum coordination species, dispersing the molybdenum component in the system in the form of peroxy coordination. Subsequently, the introduced cerium, yttrium, and zirconium salts gradually hydrolyze under the regulation of sodium bicarbonate, forming intermediate coordination units mainly composed of hydroxylated metal ions. As the system temperature increases, hydroxyl condensation, oxygen bridging, and coordination rearrangement further occur between different metal centers. The molybdenum species are embedded in the inorganic aggregate intermediates composed of cerium, yttrium, and zirconium through coordination exchange or co-deposition, gradually forming a multi-metal composite structure containing Ce-O, YO, Zr-O, and Mo-O phase key coordination units. After solid-liquid separation, drying, and granulation, a cerium-yttrium-zirconium-molybdenum composite powder with a relatively uniform composition distribution is obtained.

[0087] The working principle of cerium-yttrium-zirconium-molybdenum interface-modified composite powder in multi-element alloy-based powders is as follows:

[0088] In this process, the cerium-yttrium-zirconium-molybdenum interface-modified composite powder obtained in step one essentially corresponds to the composite structure source of interface-regulating components in the multi-element alloy-based powder. Among them, Ce, Y, and Zr components mainly provide the boundary stability basis and transition support unit of the interface region, while the Mo component participates in the synergistic regulation of the local structure near the interface. Together, the four constitute a modified phase source with a certain boundary coordination ability and structural buffering ability. After the composite powder enters the system, it does not simply increase the content of a certain element, but tends to be distributed in the contact area of ​​different particles, the transition area of ​​the structure, and the vicinity of the boundary formed by subsequent sintering. This improves the continuity of the connection between multiple components, weakens the abrupt change of interface properties, and helps to reduce the weak parts formed by insufficient structure connection in local areas. As a result, the final multi-element alloy-based powder is more likely to maintain coordination in terms of interparticle interlocking state, structural boundary integrity after sintering, and stress transmission uniformity under service load. Furthermore, it forms a more stable interface structure basis for controlling the opening rate of automotive gears and reducing the pitting corrosion of single teeth and the pitting corrosion area ratio of gear pairs.

[0089] Step 2: Preparation of composite substrate mixed powder

[0090] By weight, 78 parts of zirconium-based hexa-elemental framework composite powder prepared in Example 1, 14 parts of aluminum-titanium-niobium reinforced composite powder prepared in Example 4, and 5 parts of cerium-yttrium-zirconium-molybdenum interface modified composite powder were weighed and added to a mixer for mixing. After being mixed evenly, the mixture was ground through an 80-mesh sieve to obtain composite substrate mixed powder.

[0091] Step 3: Preparation of multi-element alloy-based powder

[0092] The composite substrate powder was placed in a corundum boat and then transferred to a tube furnace. Under a vacuum of -0.098 MPa, the temperature was raised to 380°C and held for 40 minutes. Then, a mixed gas of hydrogen and argon at a volume ratio of 1:6 was introduced, and the temperature was raised to 880°C and held for 1 hour. Then, the temperature was switched to a vacuum of -0.098 MPa and raised to 1080°C and held for 40 minutes. After the holding period, the temperature was lowered to 150°C and the material was removed from the furnace. The material was crushed and mechanically pulverized, then passed through a 200-mesh sieve. The sieve residue was collected to obtain a multi-element alloy base powder.

[0093] The reaction principle for preparing multi-element alloy-based powders is as follows:

[0094] In the composite matrix mixed powder, the precursor components initially coexist in the form of oxides, hydroxylates, coordinating residues, and a small amount of salt-derived structures. Upon heating, they gradually undergo desorption, dehydration, dehydroxylation, decomposition, and removal of organic residues, resulting in a rearrangement of the metal-oxygen, metal-fluorine, and coordination bond structures in the system. Under the action of a hydrogen / argon mixed atmosphere, some of the more easily reduced metal components and their oxygen-containing species undergo reduction transformation. Under subsequent high temperature and vacuum conditions, solid-phase diffusion, mutual solubility, and interface reconstruction further occur between different components, causing the originally dispersed multi-metal units to gradually evolve into a multi-metal-based powder system dominated by alloying components, ultimately forming a multi-element alloy-based powder.

[0095] Example 8

[0096] This embodiment provides a method for preparing powder alloy for automotive gear manufacturing, including the following steps:

[0097] Step 1: Preparation of cerium-yttrium-zirconium-molybdenum interface-modified composite powder

[0098] Weigh out 3.5g of cerium nitrate hexahydrate, 1.2g of yttrium nitrate hexahydrate, and 5.5g of zirconium oxychloride octahydrate, and mix them with 100.0mL of deionized water to obtain a metal salt solution;

[0099] Weigh out 5.0 g of sodium molybdate dihydrate and 120.0 mL of deionized water and add them to the reaction vessel. Stir and mix well. Then add 9.0 mL of 30 wt% hydrogen peroxide aqueous solution. Stir the reaction vessel at 12 °C for 30 min. Then add 100.0 mL of metal salt solution and mix well. Raise the temperature to 45 °C and add 8.0 g of sodium bicarbonate. Continue to raise the temperature to 70 °C and keep stirring for 2 h. After the reaction is complete, filter and collect the filter cake. Dry the cake and pass it through a 120 mesh sieve to obtain cerium-yttrium-zirconium-molybdenum interface modified composite powder.

[0100] Step 2: Preparation of composite substrate mixed powder

[0101] By weight, 82 parts of zirconium-based hexa-elemental framework composite powder prepared in Example 2, 20 parts of aluminum-titanium-niobium reinforced composite powder prepared in Example 5, and 9 parts of cerium-yttrium-zirconium-molybdenum interface modified composite powder were weighed and added to a mixer for mixing. After being mixed evenly, the mixture was ground through a 120-mesh sieve to obtain composite substrate mixed powder.

[0102] Step 3: Preparation of multi-element alloy-based powder

[0103] The composite substrate powder was placed in a corundum boat and then transferred to a tube furnace. Under a vacuum of -0.098 MPa, the temperature was raised to 430°C and held for 60 minutes. Then, a mixed gas of hydrogen and argon at a volume ratio of 1:10 was introduced, and the temperature was raised to 960°C and held for 2 hours. The temperature was then switched to a vacuum of -0.098 MPa and raised to 1140°C and held for 60 minutes. After the holding period, the temperature was lowered to 250°C and the material was removed from the furnace. The material was crushed and mechanically pulverized, then passed through a 320-mesh sieve. The undersize material was collected to obtain a multi-element alloy base powder.

[0104] Example 9

[0105] This embodiment provides a method for preparing powder alloy for automotive gear manufacturing, including the following steps:

[0106] Step 1: Preparation of cerium-yttrium-zirconium-molybdenum interface-modified composite powder

[0107] Weigh out 3.0 g of cerium nitrate hexahydrate, 1.0 g of yttrium nitrate hexahydrate, and 5.0 g of zirconium oxychloride octahydrate, and mix them with 100.0 mL of deionized water to obtain a metal salt solution;

[0108] Weigh 4.5g of sodium molybdate dihydrate and 120.0mL of deionized water and add them to the reaction vessel. Stir and mix well. Then add 8.0mL of 30wt% hydrogen peroxide aqueous solution. Stir the reaction vessel at 10℃ for 25min. Then add 100.0mL of metal salt solution and mix well. Raise the temperature to 40℃ and add 7.0g of sodium bicarbonate. Continue to raise the temperature to 65℃ and keep stirring for 2h. After the reaction is complete, filter and collect the filter cake. After drying, pass it through a 120-mesh sieve to obtain cerium-yttrium-zirconium-molybdenum interface modified composite powder.

[0109] Step 2: Preparation of composite substrate mixed powder

[0110] By weight, 80 parts of the zirconium-based six-element framework composite powder prepared in Example 3, 18 parts of the aluminum-titanium-niobium reinforced composite powder prepared in Example 6, and 7 parts of cerium-yttrium-zirconium-molybdenum interface modified composite powder were weighed and added to a mixer for mixing. After being mixed evenly, the mixture was ground through a 100-mesh sieve to obtain composite substrate mixed powder.

[0111] Step 3: Preparation of multi-element alloy-based powder

[0112] The composite substrate powder was placed in a corundum boat and then transferred to a tube furnace. Under a vacuum of -0.098 MPa, the temperature was raised to 400°C and held for 50 minutes. Then, a mixed gas of hydrogen and argon at a volume ratio of 1:8 was introduced, and the temperature was raised to 920°C and held for 2 hours. Then, the temperature was switched to a vacuum of -0.098 MPa and raised to 1120°C and held for 50 minutes. After the holding period, the temperature was lowered to 200°C and the material was removed from the furnace. The material was crushed and mechanically pulverized, then passed through a 250-mesh sieve. The sieve residue was collected to obtain a multi-element alloy base powder.

[0113] Comparative Example 1

[0114] The difference between this comparative example and Example 9 is that step II of the zirconium-based hexa-elemental framework composite powder used in step II is omitted during the preparation process, and the hexa-elemental metal fluorine-containing precursor prepared in step I is used as an equal substitute.

[0115] Comparative Example 2

[0116] The difference between this comparative example and Example 9 is that step ② of the aluminum-titanium-niobium reinforced composite powder used in step 2 is omitted during the preparation process, and the aluminum-titanium-niobium reinforced precursor prepared in step ① is used instead.

[0117] Comparative Example 3

[0118] The difference between this comparative example and Example 9 is that the use of cerium-yttrium-zirconium-molybdenum interface-modified composite powder is omitted in step two.

[0119] Performance testing:

[0120] The tap density of the multi-element alloy-based powders prepared in Examples 7-9 and Comparative Examples 1-3 was tested in accordance with the standard GB / T 5162-2021 "Determination of tap density of metal powders".

[0121] The loose density of the multi-element alloy-based powders prepared in Examples 7-9 and Comparative Examples 1-3 was tested in accordance with the standard GB / T 1479.1-2011 "Determination of loose density of metal powders - Part 1: Funnel method".

[0122] Powder metallurgy spur gears prepared using multi-element alloy-based powders in Examples 7-9 and Comparative Examples 1-3 have the following structural parameters: module m = 1.50 mm, number of teeth z = 24, pressure angle 20°, helix angle 0°, displacement coefficient x = 0, tooth width b = 18.0 mm, pitch circle diameter d = 36.0 mm, addendum circle diameter da = 39.0 mm, dedendum circle diameter df = 32.25 mm, inner diameter φ16.0 mm, hub outer diameter φ28.0 mm, and hub thickness 18.0 mm. The compact mass was controlled at 52.80g. During preparation, 1000.0g of multi-element alloy-based powder was weighed, and 6.0g of vinyl bis-stearamide was added. The mixture was then mixed at 22rpm for 30min in a V-type mixer, followed by vacuum drying at 80℃ for 2h. After granulation through a 100-mesh sieve, the powder was loaded into a gear pressing mold. Before pressing, the mold was preheated to 60℃ and the powder to 50℃. The powder was then formed using a mechanical press with bidirectional pressing at a pressure of 750MPa, a holding time of 2.0s, and a demolding speed of 10mm / s, yielding a green compact with a density of 6.92g / cm³. 3 Gear blanks were prepared; the resulting blanks were placed in a degreasing furnace and heated to 200℃ at 5℃ / min under a 95% N2 + 5% H2 atmosphere, and held for 20 min, then heated to 600℃ at 3℃ / min and held for 30 min to complete degreasing; after degreasing, the blanks were transferred to a vacuum sintering furnace and heated to 1220℃ at 9℃ / min under a vacuum of 8 Pa, held for 60 min, and then cooled, with the cooling rate controlled at 1.5℃ / s during the 1220℃ to 600℃ stage. After cooling to room temperature, sintered automotive gear blanks were obtained with a sintering density of 7.18 g / cm³. 3 ;

[0123] The porosity of automotive gears prepared from the multi-element alloy-based powders prepared in Examples 7-9 and Comparative Examples 1-3 was tested in accordance with the standard GB / T 5163-2006 "Determination of density, oil content and porosity of permeable sintered metal materials (excluding cemented carbide)".

[0124] The pitting area ratio of a single tooth and the pitting area ratio of a gear pair were tested according to the standard GB / T 14229-2021 "Test Method for Contact Fatigue Strength of Gears".

[0125] See Table 1 for specific data;

[0126] Table 1 - Performance Test Data for Each Sample

[0127] Project Group Example 7 Example 8 Example 9 Comparative Example 1 Comparative Example 2 Comparative Example 3 <![CDATA[Tap density / g·cm -3 > 7.16 7.16 7.17 6.97 7.03 7.08 <![CDATA[Bulk density / g·cm -3 > 5.82 5.83 5.83 5.59 5.68 5.74 Open area ratio / % 1.56 1.55 1.54 1.87 2.06 1.93 Single tooth pitting area ratio / % 0.45 0.43 0.43 0.71 0.82 0.95 Pitching area ratio of gear pair / % 0.98 0.97 0.97 1.49 1.67 1.92

[0128] Data Analysis:

[0129] A comparative analysis of the data in Table 1 reveals that the tap density of the multi-element alloy-based powder prepared in this invention is 7.17 g·cm³. -3 The loose bulk density is 5.83 g·cm³. -3 Furthermore, the automotive gears prepared using this multi-element alloy-based powder exhibit an open area ratio of 1.54%, a single-tooth pitting area ratio of 0.43%, and a gear pair pitting area ratio of 0.97%. All these data are superior to the comparative example, indicating that:

[0130] In Comparative Example 1, the hexa-metal fluorine-containing precursor obtained in step I directly replaced the framework composite powder constructed in step II. This caused the system to lose the particle hierarchical support relationship and spatial bearing unit formed in the subsequent framework process. As a result, it was difficult for the composite substrate powder to establish a relatively stable particle interlocking state during the mixing, sieving and pressing stages. Local areas were more prone to filling differences and inconsistent densification starting points. This inhomogeneity continued to be transmitted to the subsequent reduction, alloying and sintering stages, which easily caused the shrinkage pace of different areas to be uncoordinated, the pore closing path to be discontinuous, and the local weak parts in the final structure to be more easily retained. The above-mentioned structural evolution deviations further affected the continuity of stress transmission under load, and thus the overall composite performance of the sample decreased.

[0131] In Comparative Example 2, the aluminum-titanium-niobium reinforced precursor obtained in step ① was used to directly replace the reinforced composite powder treated in step ②. This caused the system to lose the rearrangement and solidification process corresponding to the further evolution of the precursor into a stable reinforced structure. Since this process was not completed, it was difficult to maintain a consistent distribution of the relevant components in the composite substrate and the stability of the contact boundary. The synchronicity of the reaction in different regions during the subsequent heat treatment was also affected. As a result, the continuity of the microstructure during the sintering stage was weakened, and the pore shrinkage and structural integration processes were not easily promoted in a coordinated manner. Local areas were more prone to insufficient microstructure connection or discontinuous load-bearing units. The above differences were further transmitted to the service loading stage, causing the stress diffusion path to become more discrete, which ultimately resulted in a decline in the composite performance of the sample.

[0132] In Comparative Example 3, step two did not introduce cerium-yttrium-zirconium-molybdenum interface-modified composite powder, causing the system to lose the original interface transition and boundary adjustment links between multi-component particles. Due to the lack of such progressive interface coordination, the contact area formed by the skeleton component and the reinforcing component during mixing, heat treatment and sintering is more likely to show a hard transition and insufficient connection. The continuity of the structure at the local boundary is thus restricted. This boundary difference will further affect the integration mode of the structure around the pores during the densification process, and become the preferred area for stress concentration and damage propagation under subsequent loading. As a result, the integrity of the transmission chain from powder configuration, sintered structure to service interface inside the material is weakened, and the composite performance of the sample decreases accordingly.

[0133] In conclusion, the material system in this application is not a simple parallel use of several functional powders, but rather a composite configuration path with sequential connections established around three levels: skeleton structure formation, reinforcement structure evolution, and interface transition coordination. Among them, the skeleton composite powder corresponds to the stable establishment of particle packing state, compression response, and subsequent densification initiation; the reinforcement composite powder corresponds to the microstructure integration, load-bearing unit formation, and structural continuity process during heat treatment and sintering; and the interface modification composite powder participates in the boundary transition between components from different sources, the local stress transfer, and the regulation of damage propagation paths during service.

[0134] The joint introduction of the three components in step two is not only reflected in the compositional relationship, but also in the continuous action chain from powder mixing, pressing, sintering to service loading. Correspondingly, when any one of the links is replaced by the precursor state, the construction process is simplified, or it is completely eliminated, the material system will show different degrees of deviation in terms of particle rearrangement, microstructure evolution and boundary coordination, and the sample performance will show a downward tendency. The above comparison relationship makes the internal relationship between the overall concept of the technical solution, the material configuration method and the operation process more complete.

[0135] The above description is merely an example and illustration of the structure of the present invention. Those skilled in the art can make various modifications or additions to the specific embodiments described, or use similar methods to replace them, as long as they do not deviate from the structure of the invention or exceed the scope defined in the claims, all of which should fall within the protection scope of the present invention.

[0136] In the description of this specification, references to terms such as "an embodiment," "example," "specific example," etc., indicate that a specific feature, structure, material, or characteristic described in connection with that embodiment or example is included in at least one embodiment or example of the invention. In this specification, illustrative expressions of the above terms do not necessarily refer to the same embodiment or example. Furthermore, the specific features, structures, materials, or characteristics described may be combined in any suitable manner in one or more embodiments or examples.

[0137] The preferred embodiments of the present invention disclosed above are merely illustrative of the invention. These preferred embodiments do not exhaustively describe all details, nor do they limit the invention to specific implementations. Clearly, many modifications and variations can be made based on the content of this specification. This specification selects and specifically describes these embodiments to better explain the principles and practical applications of the invention, thereby enabling those skilled in the art to better understand and utilize the invention. The invention is limited only by the claims and their full scope and equivalents.

Claims

1. A powder alloy for manufacturing automotive gears, characterized in that, The raw material composition includes the following parts by weight: 78-82 parts zirconium-based six-element framework composite powder, 14-20 parts aluminum-titanium-niobium reinforced composite powder and 5-9 parts cerium-yttrium-zirconium-molybdenum interface modified composite powder; The preparation method of the zirconium-based six-membered framework composite powder is as follows: a six-membered metal fluorine-containing precursor, zirconium oxychloride octahydrate, anhydrous sodium acetate, ethylene glycol and deionized water are added to a reaction vessel and stirred. After mixing evenly, the reaction vessel is heated to 75-85℃ and stirred for 30-60 minutes. Then, the coordination component is added, and the temperature is further increased to 105-115℃ and stirred for 2-3 hours. The zirconium-based six-membered framework composite powder is obtained after post-treatment.

2. The powder alloy for manufacturing automotive gears according to claim 1, characterized in that, In the preparation of zirconium-based hexa-elemental framework composite powder, the ratio of the hexa-elemental metal fluorine-containing precursor, zirconium oxychloride octahydrate, anhydrous sodium acetate, ethylene glycol, deionized water and coordination component is 16-20g:5-7g:4-5g:100mL:50mL:4-6mL, wherein the coordination component is an 80wt% hydrazine aqueous solution.

3. The powder alloy for manufacturing automotive gears according to claim 1, characterized in that, The preparation method of the hexa-metal fluorine-containing precursor is as follows: add multi-metal hydrate, ethylene glycol and deionized water into a reaction vessel and stir. After mixing evenly, add ammonium fluoride and citric acid, then heat the reaction vessel to 58-65℃ and stir for 40-60 min. Then continue to heat to 75-85℃ and stir for 2-3 h. After the reaction is completed, filter, collect the filter cake and dry it to obtain the hexa-metal fluorine-containing precursor.

4. The powder alloy for manufacturing automotive gears according to claim 3, characterized in that, In the preparation of the hexa-metal fluorine-containing precursor, the ratio of the multi-metal hydrate, ethylene glycol, deionized water, ammonium fluoride, and citric acid is 28-38g:120mL:80mL:2-3g:5-7g. The multi-metal hydrate is obtained by mixing ferric chloride hexahydrate, nickel chloride hexahydrate, cobalt chloride hexahydrate, chromium nitrate nonahydrate, ammonium heptamolybdate tetrahydrate, and niobium pentachloride in a ratio of 7-9g:6-8g:4-6g:5-7g:4-5g:2-3g.

5. The powder alloy for manufacturing automotive gears according to claim 1, characterized in that, The aluminum-titanium-niobium reinforced composite powder is prepared by the following method: A1. Add anhydrous ethanol and deionized water to the reactor and stir. Then add aluminum nitrate nonahydrate and niobium pentachloride. After mixing evenly, add isopropyl titanate, then add peroxide component and triethyl phosphate. Stir the reactor at 5-10℃ for 40-60 min. Then raise the temperature to 35-40℃ and stir for 60-80 min. Then raise the temperature to 60-70℃ and stir for 1-2 h. The post-processing yields aluminum-titanium-niobium reinforced precursor. A2. Add the aluminum-titanium-niobium reinforced precursor, diethylenetriamine and formamide to the reaction vessel and stir. After mixing evenly, heat the reaction vessel to 90-95℃ and stir for 1-2 hours. Then continue to heat to 125-135℃ and stir for 40-60 minutes. After the reaction is completed, distill under reduced pressure until no liquid is collected to obtain aluminum-titanium-niobium reinforced composite powder.

6. The powder alloy for manufacturing automotive gears according to claim 5, characterized in that, In step A1, the ratio of anhydrous ethanol, deionized water, aluminum nitrate nonahydrate, niobium pentachloride, isopropyl titanate, peroxide component, and triethyl phosphate is 120 mL:30 mL:4-5 g:1-2 g:4-5 mL:4-5 mL:5-6 mL, wherein the peroxide component is a 30 wt% aqueous solution of hydrogen peroxide; in step A2, the ratio of aluminum-titanium-niobium reinforced precursor, diethylenetriamine, and formamide is 14-18 g:7-9 mL:70-90 mL.

7. The powder alloy for manufacturing automotive gears according to claim 1, characterized in that, The preparation method of the cerium-yttrium-zirconium-molybdenum interface-modified composite powder is as follows: sodium molybdate dihydrate and deionized water are added to a reaction vessel and stirred. After mixing evenly, 30wt% hydrogen peroxide aqueous solution is added. The reaction vessel is stirred for 12-30 minutes at 8-12℃. Then, a metal salt solution is added and mixed evenly. The temperature is raised to 35-45℃ and sodium bicarbonate is added. The temperature is then raised to 60-70℃ and stirred for 1-2 hours. After the reaction is completed, the filter cake is collected, dried, and passed through a 120-mesh sieve to obtain the cerium-yttrium-zirconium-molybdenum interface-modified composite powder.

8. The powder alloy for manufacturing automotive gears according to claim 7, characterized in that, In the preparation of the cerium-yttrium-zirconium-molybdenum interface-modified composite powder, the ratio of sodium molybdate dihydrate, deionized water, 30wt% hydrogen peroxide aqueous solution, metal salt solution, and sodium bicarbonate is 4-5g:120mL:7-9mL:100mL:6-8g. The metal salt solution is obtained by mixing cerium nitrate hexahydrate, yttrium nitrate hexahydrate, zirconium oxychloride octahydrate, and deionized water in a ratio of 2.5-3.5g:0.8-1.2g:4.5-5.5g:100mL.

9. A method for preparing a powder alloy for automotive gear manufacturing as described in any one of claims 1-8, characterized in that, Includes the following steps: S1. Weigh out the following by weight: zirconium-based six-element framework composite powder, aluminum-titanium-niobium reinforced composite powder and cerium-yttrium-zirconium-molybdenum interface modified composite powder, add them to a mixer and mix them. After mixing evenly, grind them through an 80-120 mesh sieve to obtain composite substrate mixed powder. S2. The composite substrate mixed powder is placed in a corundum boat and then transferred to a tube furnace. Under vacuum conditions, the temperature is raised to 380-430℃ and held for 40-60 minutes. Then, mixed gas is introduced and the temperature is raised to 880-960℃ and held for 1-2 hours. Then, the temperature is raised to 1080-1140℃ under vacuum conditions and held for 40-60 minutes. The post-processing yields multi-element alloy base powder.

10. The method for preparing a powder alloy for automotive gear manufacturing according to claim 9, characterized in that, In step S2, the vacuum level is -0.098 MPa, and the mixed gas is obtained by mixing hydrogen and argon in a volume ratio of 1:6-10.

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