Slurry pump body of lining splicing type composite ceramic volute

Abstract

The invention belongs to the field of slurry pumps, and particularly relates to a slurry pump body of a lining splicing type composite ceramic volute, which comprises a lining layer, the lining layer comprises a plurality of lining splicing blocks I, and the lining splicing blocks I are connected through lining splicing blocks II; an L-shaped connecting groove I is formed in the inner side of one end of the lining splicing block I, and an inclined slot I is formed in the inner side of the other end; second L-shaped connecting grooves are formed in the outer sides of one ends of the second lining splicing blocks, and second inclined inserting grooves are formed in the outer sides of the other ends of the second lining splicing blocks; the first inclined inserting groove of one first lining splicing block and the second inclined inserting groove in one end of the second lining splicing block are buckled together in an inclined mode, and the first L-shaped connecting groove of the other first lining splicing block and the second L-shaped connecting groove in the other end of the second lining splicing block are buckled together in a staggered mode. By means of thrust generated by fluid flowing, the first inclined inserting groove is promoted to be inserted into the second inclined inserting groove better, and the first inclined inserting groove and the second inclined inserting groove are buckled and sealed more obliquely. And the first L-shaped connecting groove and the second L-shaped connecting groove are buckled and sealed better.

Description

Technical Field

[0001] This invention relates to the field of slurry pumps, specifically to a slurry pump body with an internally lined composite ceramic volute. Background Technology

[0002] Slurry pumps, as core power equipment for conveying solid-liquid two-phase or highly corrosive media, utilize the centrifugal force generated by impeller rotation to pressurize and transport abrasive slurries. They are widely used in mining, metallurgy, power, dredging, and chemical industries. Because the media they handle often contain high-hardness, high-concentration solid particles and may be chemically corrosive, the pump casing's inner wall is subjected to severe scouring, abrasion, and corrosion over long periods. Therefore, its durability and reliability directly determine the equipment's service life, operational safety, and maintenance costs.

[0003] To cope with extreme operating conditions, modern high-performance slurry pumps generally incorporate wear-resistant and corrosion-resistant linings on the inner walls of the pump casing (primarily the volute and diffuser). Among these, linings made of ceramic materials (such as silicon carbide and alumina) have become an important development direction due to their extremely high hardness and excellent corrosion resistance. However, the complex structure and significant curvature variations of the pump casing volute make the large-sized, irregularly shaped ceramic lining extremely difficult to fire, leading to deformation, cracking, and ultimately low yield and high manufacturing costs. Therefore, the industry has proposed a "lining splicing" design approach, which involves breaking down the lining layer into multiple relatively regularly shaped small ceramic pieces, which are then assembled using a splicing method to reduce the difficulty of firing individual pieces and improve the yield.

[0004] While the spliced ​​design of the lining alleviates the manufacturing difficulties to some extent, it introduces a new technical bottleneck: the splicing seams become the structural weak points of the lining layer. For example, in the patent application No. 202220851560.8, "A Slurry Pump Body with an Inner Lined Spliced ​​Composite Ceramic Volute", although the difficulty of overall firing was solved by using a large number of small inner lining pieces for splicing, the numerous joints face severe challenges during long-term service. When high-velocity, high-hardness solid particle slurry flows through the joints, a "micro-jet" effect is formed, generating continuous impact and shearing action on the joint edges. This not only easily leads to micro-chipping at the edges of the ceramic blocks, accelerating local wear, but more seriously, the fluid may infiltrate the interior of the joints, eroding the underlying adhesive or volute matrix material, weakening the overall bonding strength. In addition, under alternating loads (such as start-up and shutdown impacts, pressure pulsations), stress is easily concentrated at the joints, which may induce the initiation of micro-cracks and their propagation along the joints, eventually leading to local or even large-area detachment of the inner lining layer, seriously affecting the pump body's sealing performance, wear resistance, and service life. Summary of the Invention

[0005] Regarding the existing composite ceramic volute with interlocking inner linings, the seams at the joints are subject to long-term scouring and impact from high-velocity, high-hardness solid particles ("micro-jet"), which can lead to fluid intrusion into the seams, causing microscopic chipping at the edges of the ceramic blocks, erosion of the underlying adhesive or volute matrix, and potential crack propagation under alternating loads. To achieve the above objectives, this invention provides the following technical solution:

[0006] The pump body of a slurry pump with an interlocking composite ceramic volute includes a pump casing with a discharge pipe. An inner lining layer is laid inside the pump casing. The inner lining layer includes multiple interlocking blocks (I), which are arranged in a ring array inside the pump casing. The multiple interlocking blocks (I) are connected to each other by interlocking blocks (II). Both interlocking blocks (I and II) are arc-shaped. Interlocking block (I) includes a block body (I), with an L-shaped connecting groove on the inner side of one end and a slanted slot on the inner side of the other end. Interlocking block (II) includes... The second splicing block has an L-shaped connecting groove on one side and an oblique slot on the other side. The oblique slot 1 of one inner lining splicing block and the oblique slot 2 at one end of the second inner lining splicing block are obliquely engaged together. The L-shaped connecting groove 1 of another inner lining splicing block and the L-shaped connecting groove 2 at the other end of the second inner lining splicing block are misaligned and engaged together. The engaging unit of the oblique slot 1 and the oblique slot 2 is located behind the engaging unit of the L-shaped connecting groove 1 and the L-shaped connecting groove 2. The inclination of the oblique slot 1 and the oblique slot 2 is the same as the fluid flow direction inside the slurry pump casing.

[0007] The inner lining layer is composed of multiple inner lining splicing blocks 1 and multiple inner lining splicing blocks 2, which reduces the firing difficulty and increases the yield. The two ends of inner lining splicing blocks 1 and 2 are respectively spliced ​​through fastening units formed by oblique slots 1 and 2, and through fastening units formed by L-shaped connecting grooves 1 and 2, achieving a staggered fastening direction perpendicular to the fluid flow direction. Because the fastening units of oblique slots 1 and 2 are located behind the fastening units of L-shaped connecting grooves 1 and 2, the fluid first passes through the fastening units of oblique slots 1 and 2, and then through L-shaped connecting grooves 1 and 2. The locking unit of L-shaped connecting groove 2 utilizes the thrust generated by fluid flow to push the first inclined slot into the second inclined slot, causing the first and second inclined slots to lock together more tightly and seal. It also causes the first and second L-shaped connecting grooves to lock together more tightly and seal. Under long-term exposure to the micro-jet scouring and impact of high-velocity, high-hardness solid particles, the joint at the splice will lock together more tightly, reducing the risk of fluid intrusion into the joint, preventing micro-chipping at the edge of the ceramic block, erosion of the underlying adhesive or vortex chamber matrix, and crack propagation.

[0008] Preferably, the inner side of the second splicing block is provided with a protrusion, and a wedge-shaped surface is provided on the protrusion. The wedge-shaped surface is used to interact with the fluid to generate a pushing force on the second splicing block, which promotes the closer engagement of the first and second oblique slots, as well as the closer engagement of the first and second L-shaped connecting grooves.

[0009] Preferably, ceramic lining splicing structures are laid between the inner lining splicing block one and the inner lining splicing block two and the slurry pump casing, between the inclined slot one and the inclined slot two, and between the L-shaped connecting slot one and the L-shaped connecting slot two. The ceramic lining splicing structure includes a ceramic lining, a metal substrate, and joint material filling the gaps therebetween.

[0010] Preferably, the joint material is a metal-ceramic composite material with multi-stable phase transformation capability and biomimetic gradient topology, and its cured body includes a multi-stable composite matrix, a five-level biomimetic gradient interface system, and an integrated response unit.

[0011] Preferably, the multistable composite matrix is ​​a double continuous three-dimensional interpenetrating network formed by shape memory alloy powder, stainless steel powder and nano-oxide ceramic powder through spark plasma sintering, wherein the volume fraction of the metal phase is 55%-65% and the ceramic phase is 35%-45%. The multistable composite matrix has at least two stable states that can be mutually converted by temperature or stress triggering, corresponding to a high stiffness state, a high toughness state and a high damping state, respectively.

[0012] The five-level biomimetic gradient interface system includes a self-assembled monolayer bridge at the metal / ceramic phase interface, a nano-anchoring formed by carbon nanotube arrays grown from the surface of ceramic particles, a SiC whisker layer with gradient orientation controlled by a magnetic field, a mesoscopic transition layer composed of gradient-distributed micropores and hollow ceramic microspheres, and a hyperbolic paraboloid macroscopic geometric topology.

[0013] The integrated response unit includes fluorescent rare earth complex microcapsules for damage visualization and early warning, a dual-channel self-healing system comprising chemical repair microcapsules and shape memory alloy physical repair based on Joule heating effect, and a thermal expansion intelligent management unit composed of negative thermal expansion material microregions and phase change microcapsules.

[0014] The chemical composition, porosity, reinforcing phase orientation, thermal expansion coefficient, and functional unit concentration of the joint material in the thickness direction all exhibit a continuous nonlinear gradient change. Furthermore, this gradient distribution is designed for specific ceramic-metal systems through finite element analysis and machine learning optimization algorithms to minimize multi-physics stress during service.

[0015] Preferably, in the multistable composite matrix, the shape memory alloy powder is Ni. 47 Ti 44Nb9 (at.%) powder, austenite finishing temperature Af of 70℃±5℃, particle size 0.5-2 μm; stainless steel powder 316L, particle size 1-3 μm; nano-oxide ceramics are a mixture of 3mol% Y2O3-stabilized ZrO2 and α-Al2O3, with average particle sizes of 30-50 nm and 100-200 nm, respectively, and a molar ratio of 7:3; the spark plasma sintering process parameters are: sintering temperature 1250-1350℃, pressure 60-80 MPa, holding time 5-8 min, heating rate 100-200 ℃ / min.

[0016] Preferably, in the five-level biomimetic gradient interface system:

[0017] The self-assembled monolayer is 12-octadecylphosphonic acid, in which the phosphonic acid groups are bonded to the ceramic phase surface and the alkyl chains are bonded to the metal phase surface.

[0018] The carbon nanotube array consists of multi-walled carbon nanotubes grown in situ on the surface of ceramic particles via chemical vapor deposition. These nanotubes have a diameter of 10-20 nm, a length of 200-500 nm, and an areal density of 20-40 nanotubes / μm. 2 ;

[0019] The orientation gradient of SiC whiskers is as follows: in the first surface region, which is close to the ceramic liner and has a thickness of 0-30%, the long axis of the whiskers is parallel to the surface; in the transition region, which has a thickness of 30-70%, the long axis of the whiskers is staggered with the surface normal at 45°±10°; and in the second surface region, which is close to the metal matrix and has a thickness of 70-100%, the long axis of the whiskers is perpendicular to the surface.

[0020] The equation for the macroscopic geometric topology of a hyperbolic paraboloid is: z = x² / a² - y² / b², where the values ​​of a and b are designed according to the joint width and depth, and the a / b ratio is between 1.5 and 3.0.

[0021] Preferably, in the integrated response unit:

[0022] The wall material of the fluorescent rare earth complex microcapsules is polymethyl methacrylate, with a particle size of 5-15 μm. They contain a mixture of Eu(TTA)3Phen and Tb(AA)3Phen complexes. Under ultraviolet light excitation, they emit red light at 614 nm and green light at 545 nm, respectively. The fluorescence intensity increases more than 10 times after the microcapsules rupture.

[0023] The chemical repair microcapsules contain active components of terminal vinyl siloxane prepolymer and platinum catalyst microcapsules. The repair agent can be cured within 30 minutes after release and can repair cracks with a width of no more than 20 μm.

[0024] The physical repair system based on the Joule heating effect includes a three-dimensional conductive network of graphene / carbon nanotubes pre-embedded in the material. The network has a volume resistivity of 0.1-1 Ω·cm. Applying a 5-10 V pulse voltage for 1-5 s can generate a local temperature rise of 100-150℃, which activates the phase transition recovery of the shape memory alloy.

[0025] The negative thermal expansion material micro-regions are ZrW2O8 with a particle size of 2-5 μm and a volume fraction of 5-10%. The phase change microcapsules have a paraffin / urea-formaldehyde resin core-shell structure and a phase change temperature range of 60-120℃.

[0026] Preferably, the ceramic liner is Al2O3, SiC or ZrO2 ceramic, with a thickness of 5-30 mm and a surface roughness Ra=1.6-3.2μm;

[0027] The metal matrix is ​​carbon steel, stainless steel, nickel-based high-temperature alloy or titanium alloy, with a thickness of not less than 10 mm;

[0028] The joint material fills a gap with a width of 0.3-5mm, and the thickness gradient structure matches the properties of the materials on both sides, with no abrupt changes at the interface;

[0029] Within the joint material layer of the splicing structure, a miniature wireless temperature / strain sensor node is pre-embedded every 50-100 mm along the length direction for real-time monitoring of service status.

[0030] Preferably, at the interface between the joint material layer and the ceramic liner, a 0.5-2 μm thick zirconium aluminum composite oxide solid solution transition layer is formed by atomic diffusion, and at the interface with the metal matrix, a 1-3 μm thick Fe-Ti or Ni-Ti intermetallic compound transition layer is formed. The presence of the transition layer enables the interfacial shear strength to reach 50-65 MPa at room temperature and 35-45 MPa at 600℃.

[0031] Compared with the prior art, the present invention can achieve the following:

[0032] 1. The inner lining layer is composed of multiple inner lining splicing blocks 1 and multiple inner lining splicing blocks 2, which reduces the firing difficulty and increases the yield. The two ends of inner lining splicing blocks 1 and 2 are spliced ​​by fastening units formed by oblique slots 1 and 2, and by fastening units formed by L-shaped connecting grooves 1 and 2, respectively, to achieve a staggered fastening direction perpendicular to the fluid flow direction. Since the fastening units of oblique slots 1 and 2 are located behind the fastening units of L-shaped connecting grooves 1 and 2, the fluid first passes through the fastening units of oblique slots 1 and 2, and then through the L-shaped connecting grooves. The interlocking unit of slot one and L-shaped connecting slot two utilizes the thrust generated by fluid flow to make the first inclined slot insert more into the second inclined slot, and the first and second inclined slots more inclined and interlocked for a seal; and to make the first and second L-shaped connecting slots more interlocked, and the first and second inclined slots more interlocked for a seal; under long-term exposure to the micro-jet scouring and impact of high-velocity, high-hardness solid particles, the joint at the splicing point will be more tightly interlocked, reducing the risk of fluid intrusion into the joint, avoiding micro-chipping at the edge of the ceramic block, erosion of the underlying adhesive or vortex chamber matrix, and crack propagation;

[0033] 2. During the use of the slurry pump body, due to the presence of the protrusions and wedges, they can interact with the fluid and generate a pushing force on the second splicing block, promoting a better engagement between the first and second inclined slots, as well as between the first and second L-shaped connecting slots; thus achieving a better seal between the first and second inner lining splicing blocks.

[0034] 3. When the temperature changes between -40℃ and 600℃ or when subjected to impact, NiTiNb undergoes a martensitic phase transformation to absorb energy, while 316L stainless steel provides plastic deformation capability; the ceramic phase consumes energy through stress-induced tetragonal-to-monoclinic phase transformation (t-to-m phase transformation); the phase transformation behavior of the metallic phase and the ceramic phase forms a synergy under specific temperature ranges and stress levels, enabling the material as a whole to exhibit reversible switching between three steady states of "high stiffness, high toughness, and high damping";

[0035] 4. The self-assembled monolayer is 12-octadecylphosphonic acid, with its phosphonic acid groups bonded to the ceramic phase surface and its alkyl chains bonded to the metal phase surface, achieving chemical bond bridging. Carbon nanotube arrays are grown on the surface of ceramic particles, with the other end of the carbon nanotubes embedded in the metal phase, forming a nano-anchoring effect. The SiC whiskers are controlled by a magnetic field to exhibit a gradient orientation distribution in the thickness direction: parallel arrangement on the ceramic side, staggered arrangement at 45° in the middle layer, and vertical arrangement on the matrix side. A sacrificial template method is used to introduce gradient-distributed micropores of 10-50 μm and hollow ceramic microspheres with a wall thickness of 2-5 μm, with the porosity gradually increasing from 1% on the ceramic side to 8% on the matrix side, forming a continuous transition in mechanical properties. The material as a whole exhibits a hyperbolic paraboloid geometry rather than a traditional planar joint. This negative curvature surface can convert normal pressure into tangential tensile stress, significantly improving the crush resistance.

[0036] 5. Fluorescent rare earth complex microcapsules are dispersed in the material. When microcracks larger than 5 μm are generated in the material, the stress field at the crack tip causes the microcapsules to rupture. The released complex emits visible fluorescence under ambient light, realizing visualized non-destructive testing. The negative thermal expansion material ZrW2O8 micro-regions and paraffin phase change microcapsules are introduced. When the temperature changes, the negative expansion material cancels the positive expansion, and the phase change material absorbs latent heat to achieve a zero expansion window. Attached Figure Description

[0037] Figure 1 This is a schematic diagram of the slurry pump body of the lining spliced ​​composite ceramic volute of the present invention.

[0038] Figure 2 for Figure 1 Schematic diagram of the inner lining layer;

[0039] Figure 3 for Figure 2 A structural schematic diagram of the inner lining splicing block 1;

[0040] Figure 4 for Figure 3 Schematic diagram of the structure of the inclined slot 1;

[0041] Figure 5 for Figure 3 Schematic diagram of the structure of L-shaped connecting groove 1;

[0042] Figure 6 for Figure 2 Schematic diagram of the structure of the inner lining splicing block 2;

[0043] Figure 7 for Figure 6 Schematic diagram of the structure of the L-shaped connecting groove II;

[0044] Figure 8 for Figure 6 Schematic diagram of the structure of the second inclined slot;

[0045] Figure 9 for Figure 2 A cross-sectional view of the inner lining layer;

[0046] Figure 10 for Figure 9 Enlarged view of point A in the middle.

[0047] In the picture:

[0048] 100. Discharge pipe; 200. Slurry pump casing; 300. Lining layer; 310. Lining splicing block one; 311. Splicing block body one; 312. L-shaped connecting groove one; 313. Angled slot one; 320. Lining splicing block two; 321. Splicing block body two; 322. L-shaped connecting groove two; 323. Angled slot two; 324. Protrusion. Detailed Implementation

[0049] The technical solution of the present invention will be further described in detail below with reference to specific embodiments. In the description of the present invention, unless otherwise stated, "a plurality of" means two or more.

[0050] In embodiments of the present invention, such as Figures 1-10 As shown: The pump body of the slurry pump with a liner-type composite ceramic volute includes a slurry pump shell 200 with a liquid outlet pipe 100 installed. An inner liner layer 300 is laid inside the slurry pump shell 200. The inner liner layer 300 includes multiple inner liner splicing blocks 310. The multiple inner liner splicing blocks 310 are arranged in a ring array inside the slurry pump shell 200. The multiple inner liner splicing blocks 310 are connected to each other through inner liner splicing blocks 320.

[0051] The quantity of "multiple inner lining splicing blocks 310" needs to be explained: it can be two, three, or four, etc. There is no limit to the specific number, as long as it is within ten, with four being the preferred number.

[0052] Both the first lining splicing block 310 and the second lining splicing block 320 are arc-shaped. The first lining splicing block 310 includes a splicing block body 311. An L-shaped connecting groove 312 is opened on the inner side of one end of the splicing block body 311, and a slanted slot 313 is opened on the inner side of the other end. The second lining splicing block 320 includes a splicing block body 321. An L-shaped connecting groove 322 is opened on the outer side of one end of the splicing block body 321, and a slanted slot 323 is opened on the outer side of the other end.

[0053] The oblique slot 313 of one inner lining splicing block 310 and the oblique slot 323 at one end of the inner lining splicing block 320 are engaged together at an angle; the L-shaped connecting groove 312 of another inner lining splicing block 310 and the L-shaped connecting groove 322 at the other end of the inner lining splicing block 320 are engaged together at an offset.

[0054] The engagement units of the angled slot 1 313 and the angled slot 2 323 are located behind the engagement units of the L-shaped connecting slot 1 312 and the L-shaped connecting slot 2 322 (the fluid first passes through the engagement units of the angled slot 1 313 and the angled slot 2 323, and then through the engagement units of the L-shaped connecting slot 1 312 and the L-shaped connecting slot 2 322; see reference for details). Figure 10 The inclination of the inclined slot 1 313 and inclined slot 2 323 is the same as the fluid flow direction inside the slurry pump casing 200 (see reference for details). Figure 10 );

[0055] It should be noted that one of the inner lining splicing blocks 310 has a liquid outlet hole;

[0056] Therefore, the inner lining layer 300 is composed of multiple inner lining splicing blocks 310 and multiple inner lining splicing blocks 320, which reduces the firing difficulty and increases the yield. The two ends of the inner lining splicing blocks 310 and 320 are respectively spliced ​​by fastening units formed by oblique slots 313 and 323, and by fastening units formed by L-shaped connecting grooves 312 and 322, achieving a misaligned fastening direction perpendicular to the fluid flow direction. Since the fastening units of oblique slots 313 and 323 are located at the L-shaped connecting grooves 312 and 322... Behind the engaging unit of L-shaped connecting groove 322, the fluid first passes through the engaging units of inclined slot 1 313 and inclined slot 2 323, and then through the engaging units of L-shaped connecting groove 1 312 and L-shaped connecting groove 2 322. This utilizes the thrust generated by the fluid flow to push inclined slot 1 313 further into inclined slot 2 323, resulting in a more inclined and sealed engagement; and to further engage L-shaped connecting groove 1 312 and L-shaped connecting groove 2 322, resulting in a more sealed engagement (see details for reference). Figure 10 Under long-term scouring and impact from micro-jets of high-velocity, high-hardness solid particles, the joints at the seams will be more tightly sealed, reducing the risk of fluid intrusion into the joints, avoiding micro-chipping at the edges of the ceramic block, erosion of the underlying adhesive or vortex chamber matrix, and crack propagation.

[0057] In embodiments of the present invention, such as Figure 6 and Figure 10 As shown: The inner side of the second splicing block 321 is provided with a protrusion 324. The protrusion 324 has a wedge-shaped surface. The wedge-shaped surface is used to interact with the fluid and generate a pushing force on the second splicing block 321, which promotes the better engagement of the first oblique slot 313 and the second oblique slot 323, as well as the better engagement of the first L-shaped connecting slot 312 and the second L-shaped connecting slot 322.

[0058] Therefore, during the use of the slurry pump body, due to the presence of the protrusion 324 and the wedge-shaped surface, they can interact with the fluid and generate a pushing force on the splicing block 321, promoting a better engagement between the oblique slot 313 and the oblique slot 323, as well as between the L-shaped connecting groove 312 and the L-shaped connecting groove 322; thus achieving a better fit and seal between the inner lining splicing block 310 and the inner lining splicing block 320.

[0059] In embodiments of the present invention, such as Figure 1 and Figure 10 As shown: Ceramic lining splicing structures are laid between the inner lining splicing block 310 and the inner lining splicing block 320 and the slurry pump casing 200, between the inclined slot 313 and the inclined slot 323, and between the L-shaped connecting slot 312 and the L-shaped connecting slot 322. The ceramic lining splicing structure includes a ceramic lining, a metal substrate, and joint material filling the gaps between them.

[0060] The joint material is a metal-ceramic composite material with multi-stable phase transformation capability and biomimetic gradient topology. Its cured body includes a multi-stable composite matrix, a five-level biomimetic gradient interface system, and an integrated response unit.

[0061] The multistable composite matrix is ​​a bicontinuous three-dimensional interpenetrating network formed by shape memory alloy powder, stainless steel powder and nano-oxide ceramic powder through spark plasma sintering. The volume fraction of the metal phase is 55%-65% and the ceramic phase is 35%-45%. The multistable composite matrix has at least two stable states that can be converted to each other by temperature or stress triggering, corresponding to the high stiffness state, high toughness state and high damping state, respectively.

[0062] The five-level biomimetic gradient interface system includes a self-assembled monolayer bridge at the metal / ceramic phase interface, a nano-anchoring formed by carbon nanotube arrays grown from the surface of ceramic particles, a SiC whisker layer with gradient orientation controlled by a magnetic field, a mesoscopic transition layer composed of gradient-distributed micropores and hollow ceramic microspheres, and a hyperbolic paraboloid macroscopic geometric topology.

[0063] The integrated response unit includes fluorescent rare earth complex microcapsules for damage visualization and early warning, a dual-channel self-healing system comprising chemical repair microcapsules and shape memory alloy physical repair based on Joule heating effect, and a thermal expansion intelligent management unit composed of negative thermal expansion material microregions and phase change microcapsules.

[0064] The chemical composition, porosity, reinforcing phase orientation, thermal expansion coefficient, and functional unit concentration of the joint material in the thickness direction all exhibit a continuous nonlinear gradient change. Furthermore, this gradient distribution is designed for specific ceramic-metal systems through finite element analysis and machine learning optimization algorithms to minimize multi-physics stress during service.

[0065] In the multistable composite matrix, the shape memory alloy powder is Ni. 47 Ti 44 Nb9 (at.%) powder, austenite finishing temperature Af of 70℃±5℃, particle size 0.5-2 μm; stainless steel powder 316L, particle size 1-3 μm; nano-oxide ceramics are a mixture of 3mol% Y2O3-stabilized ZrO2 and α-Al2O3, with average particle sizes of 30-50 nm and 100-200 nm, respectively, and a molar ratio of 7:3; the spark plasma sintering process parameters are: sintering temperature 1250-1350℃, pressure 60-80 MPa, holding time 5-8 min, heating rate 100-200 ℃ / min.

[0066] NiTiNb shape memory alloy ultrafine powder (particle size 0.5-2 μm, Af=65-85℃) is combined with ultrafine 316L stainless steel powder (1-3 μm) in a volume ratio of 4:6; the metallic phase forms a three-dimensional network continuous phase; nano ZrO2 (3Y-TZP, particle size 30-50nm) and Al2O3 (particle size 100-200nm) are sintered in situ to form a (Zr,Al)O2 solid solution; the ceramic phase is embedded in the metal network in a nano-island structure.

[0067] When the temperature changes from -40℃ to 600℃ or is subjected to impact, NiTiNb undergoes a martensitic phase transformation to absorb energy, while 316L stainless steel provides plastic deformation capability; the ceramic phase consumes energy through stress-induced tetragonal-to-monoclinic phase transformation (t-to-m phase transformation); the phase transformation behavior of the metallic phase and the ceramic phase forms a synergy under specific temperature ranges and stress levels, enabling the material as a whole to exhibit reversible switching between three steady states of "high stiffness, high toughness, and high damping".

[0068] The five-level biomimetic gradient interface system:

[0069] The self-assembled monolayer is 12-octadecylphosphonic acid, in which the phosphonic acid groups are bonded to the ceramic phase surface and the alkyl chains are bonded to the metal phase surface.

[0070] The carbon nanotube array consists of multi-walled carbon nanotubes grown in situ on the surface of ceramic particles via chemical vapor deposition. These nanotubes have a diameter of 10-20 nm, a length of 200-500 nm, and an areal density of 20-40 nanotubes / μm. 2 ;

[0071] The orientation gradient of SiC whiskers is as follows: in the first surface region, which is close to the ceramic liner and has a thickness of 0-30%, the long axis of the whiskers is parallel to the surface; in the transition region, which has a thickness of 30-70%, the long axis of the whiskers is staggered with the surface normal at 45°±10°; and in the second surface region, which is close to the metal matrix and has a thickness of 70-100%, the long axis of the whiskers is perpendicular to the surface.

[0072] The equation for the macroscopic geometric topology of a hyperbolic paraboloid is: z = x² / a² - y² / b², where the values ​​of a and b are designed according to the joint width and depth, and the a / b ratio is between 1.5 and 3.0.

[0073] Molecular-level interface: Introduce a self-assembled monolayer (phosphonate molecule, one end attached to metal and the other end attached to ceramic) at the metal / ceramic phase interface to achieve chemical bond bridging;

[0074] Nanoscale interface: Carbon nanotube arrays (10-20 nm in diameter and 200-500 nm in length) are grown on the surface of ceramic particles, and the other end of the carbon nanotubes is embedded in the metal phase to form a nano-anchoring effect.

[0075] Micrometer-level interface: SiC whiskers (0.5μm in diameter, aspect ratio 30-50) are controlled by a magnetic field to be distributed in a gradient orientation along the thickness direction: parallel arrangement on the ceramic side (wear resistant), staggered arrangement at 45° in the middle layer (shear resistant), and vertical arrangement on the substrate side (peel resistant).

[0076] Mesoscopic interface: The sacrificial template method is used to introduce a gradient distribution of 10-50μm micropores and hollow ceramic microspheres with a wall thickness of 2-5μm. The porosity increases from 1% on the ceramic side to 8% on the matrix side, forming a continuous transition in mechanical properties.

[0077] The material exhibits a hyperbolic paraboloid geometry rather than a traditional planar joint; this negative curvature surface can convert normal pressure into tangential tensile stress, significantly improving its crush resistance.

[0078] In the integrated response unit:

[0079] The wall material of the fluorescent rare earth complex microcapsules is polymethyl methacrylate, with a particle size of 5-15 μm. They contain a mixture of Eu(TTA)3Phen and Tb(AA)3Phen complexes. Under ultraviolet light excitation, they emit red light at 614 nm and green light at 545 nm, respectively. The fluorescence intensity increases more than 10 times after the microcapsules rupture.

[0080] The chemical repair microcapsules contain active components of terminal vinyl siloxane prepolymer and platinum catalyst microcapsules. The repair agent can be cured within 30 minutes after release and can repair cracks with a width of no more than 20 μm.

[0081] The physical repair system based on the Joule heating effect includes a three-dimensional conductive network of graphene / carbon nanotubes pre-embedded in the material. The network has a volume resistivity of 0.1-1 Ω·cm. Applying a 5-10 V pulse voltage for 1-5 s can generate a local temperature rise of 100-150℃, which activates the phase transition recovery of the shape memory alloy.

[0082] The negative thermal expansion material micro-regions are ZrW2O8 with a particle size of 2-5 μm and a volume fraction of 5-10%. The phase change microcapsules have a paraffin / urea-formaldehyde resin core-shell structure and a phase change temperature range of 60-120℃.

[0083] Dispersing fluorescent rare earth complex microcapsules (Eu) in materials 3+ / Tb 3+ When the material develops microcracks larger than 5 μm, the stress field at the crack tip causes the microcapsules to rupture, releasing the complex that emits visible fluorescence (red / green) under ambient light, enabling visualized non-destructive testing. The introduction of negative thermal expansion material ZrW2O8 microregions with paraffin phase change microcapsules allows the negative expansion material to counteract positive expansion and the phase change material to absorb latent heat, achieving a zero expansion window (CTE ≤ 1 × 10⁻⁻⁻⁶ within the 100-300℃ range).6 / K).

[0084] The gradient distribution of the joint material satisfies the following mathematical relationship:

[0085] ceramic phase volume fraction V ceramic The transition from the first surface to the second surface follows the function described below:

[0086] V ceramic(x) =V max -(V) max -V min )* (x / d) n Where x is the distance from the first surface, d is the total thickness, and V max =0.70-0.75, V min =0.25-0.30, n=1.5-2.5 (non-linear exponent);

[0087] The porosity P(x) satisfies: P(x) = P min +(P max -P min )*exp(k*x / d), where P min =0.01-0.015 (ceramic side), P max =0.06-0.08 (matrix side), k=2.0-3.0;

[0088] The coefficient of thermal expansion CTE(x) satisfies the following in the range of 25-600℃: CTE(x) = CTE ceramic +(CTE metal -CTE ceramic ) * erf(x / λ), where erf is the error function, λ is the feature length (0.2-0.3d), CTE ceramic =7.8-8.2×10 -6 / K, CTE metal =11.8-12.2×10 -6 / K.

[0089] In this embodiment of the invention, the ceramic lining is Al2O3, SiC or ZrO2 ceramic, with a thickness of 5-30 mm and a surface roughness Ra=1.6-3.2μm;

[0090] The metal matrix is ​​carbon steel, stainless steel, nickel-based high-temperature alloy or titanium alloy, with a thickness of not less than 10 mm;

[0091] The joint material fills a gap with a width of 0.3-5mm, and the thickness gradient structure matches the properties of the materials on both sides, with no abrupt changes at the interface;

[0092] Within the joint material layer of the splicing structure, a miniature wireless temperature / strain sensor node is pre-embedded every 50-100 mm along the length direction for real-time monitoring of service status.

[0093] At the interface between the joint material layer and the ceramic liner, a 0.5-2 μm thick zirconium aluminum composite oxide solid solution transition layer is formed by atomic diffusion. At the interface with the metal matrix, a 1-3 μm thick Fe-Ti or Ni-Ti intermetallic compound transition layer is formed. The presence of the transition layer enables the interfacial shear strength to reach 50-65 MPa at room temperature and 35-45 MPa at 600℃.

[0094] I. Material Preparation and Sample Processing Experiments

[0095] 1. Experimental objective: To prepare joint material samples that meet design requirements and process them into the specifications required for various standard tests.

[0096] 2. Main Equipment and Raw Materials

[0097] 2.1. Equipment: Planetary ball mill, six-nozzle digital light processing (DLP) 3D printer, custom triaxial rotary gradient magnetic field generator, spark plasma sintering (SPS) furnace, atomic layer deposition (ALD) system, vacuum impregnation equipment.

[0098] 2.2. Raw material: Ni 47 Ti 44 Nb9 pre-alloyed powder (0.5-2 μm), 316L stainless steel powder (1-3 μm), 3Y-TZPZrO2 nanopowder (30-50 nm), α-Al2O3 powder (100-200 nm), SiC whiskers (0.5 μm diameter, aspect ratio 30-50), 12-octadecylphosphonic acid, carbon nanotube growth catalyst, pore-forming agent (PMMA microspheres, 10-50 μm), hollow Al2O3 microspheres (wall thickness 2-5 μm), Eu / Tb fluorescent complex microcapsules, ZrW2O8 powder (2-5 μm), paraffin phase change microcapsules, photosensitive resin, etc.

[0099] 3. Experimental Procedure

[0100] 3.1. Slurry Preparation and Gradient Design

[0101] Based on the five-dimensional gradient function output by the finite element optimization model, six different formulations of photocurable slurry were prepared.

[0102] Ball milling and ultrasonic dispersion are used to ensure uniformity of each component, and the viscosity of the slurry is controlled at 2-5 Pa·s (25℃).

[0103] 3.2. DLP Printing and Magnetic Field Orientation

[0104] Six types of paste are fed into the DLP printer simultaneously, and the printer prints layer by layer according to the gradient function (layer thickness 20 μm).

[0105] Simultaneous activation of the three-axis rotating gradient magnetic field (B max =1.0 T, f=5 Hz), controlling the SiC whiskers to be oriented at preset angles (0°, 45°, 90°) within each layer.

[0106] 3.3. Degreasing and Sintering

[0107] The printed preform was heated to 600°C in air at a rate of 2°C / min and held for 4 hours to remove organic matter.

[0108] The degreased billet was placed in an SPS furnace and heated to 1300℃ at 100℃ / min under argon protection. A pressure of 70MPa was applied and the temperature was maintained for 6 min before cooling with the furnace.

[0109] 3.4. Post-processing

[0110] An 8 nm thick Al2O3 layer was deposited on the surface of the sintered body and in the open pores using ALD.

[0111] Epoxy resin containing fluorescent microcapsules and repair microcapsules was impregnated into the pores of the material by vacuum impregnation and cured at 80°C for 5 hours.

[0112] 4. Sample processing

[0113] Using a diamond wire cutter and a precision surface grinder, the sintered body was processed into samples that met the following national standard testing requirements:

[0114] Three-point bending specimen: 3 mm × 4 mm × 40 mm (GB / T 6569-2006);

[0115] Single-sided notched beam (SENB) specimen: 5 mm × 10 mm × 55 mm, precast notch depth 5 mm (GB / T 23806-2009);

[0116] Abrasion-resistant test specimen: Φ30 mm×10 mm (GB / T 12444-2006);

[0117] Thermal expansion test specimen: Φ6 mm × 25 mm (GB / T 4339-2008);

[0118] Cylindrical compression test specimen: Φ10 mm×15 mm (GB / T 8489-2006);

[0119] II. Core Performance Test Experiments and Data

[0120] 1. Mechanical properties and multi-steady-state behavior testing

[0121] 1.1. Test standards: GB / T 6569-2006 "Test method for bending strength of fine ceramics", GB / T 23806-2009 "Test method for fracture toughness of fine ceramics", GB / T 22315-2008 "Test method for elastic modulus and Poisson's ratio of metallic materials".

[0122] 1.2. Experimental equipment: Electronic universal testing machine (Instron 5967), equipped with high and low temperature environmental chamber (-70℃ to 600℃) and dynamic mechanical analysis (DMA) module.

[0123] 2. Experimental Procedure and Data

[0124] 2.1. Relationship between three-point bending strength and modulus-temperature: Bending strength and elastic modulus were tested at five temperature points: -40℃, 25℃, 200℃, 400℃, and 600℃. The results are shown in Table 1. The material exhibits obvious "tristable state" characteristics: high stiffness (highest E) at low temperature (-40℃); high toughness (highest bending strength and fracture work) from room temperature to medium temperature (25-200℃); and high damping (significantly increased loss factor tanδ as measured by DMA) at high temperature (400-600℃).

[0125] 2.2. Fracture toughness (K) IC )

[0126] The test was conducted using SENB samples at 25°C. K was measured. IC =14.2±0.8 MPa·m 1 / 2 It is much higher than that of conventional ceramic adhesives (3-5 MPa·m). 1 / 2 ) and metal-ceramic composites (8-10 MPa·m 1 / 2 ).

[0127] 2.3. Compressive Strength and Failure Mode

[0128] Compression tests were conducted on joint specimens with a hyperbolic paraboloid topology and conventional planar joint specimens (GB / T8489-2006). The topological specimen achieved a crush strength of 320 MPa, which is 52% higher than that of the planar specimen (approximately 210 MPa). Failure analysis showed that the topological structure successfully converted part of the normal compressive stress into tangential tensile stress, which was borne by the gradient-oriented SiC whisker network, thus delaying shear failure.

[0129] 3. Interface bonding and microstructure characterization

[0130] 3.1. Test standard: GB / T 35160.1-2017 "Test method for interfacial bonding strength of composite ceramics", scanning electron microscopy (SEM) and energy dispersive spectroscopy (EDS) analysis.

[0131] 3.2. Experimental equipment: Micromechanical testing system, field emission scanning electron microscope.

[0132] 3.3. Experimental Procedure and Data

[0133] 3.3.1. Interfacial Shear Strength

[0134] The interfacial bonding strength between the material and Al2O3 ceramic and 316L stainless steel substrates was tested. At room temperature, the interfacial strength with ceramic was 58 MPa, and with metal was 62 MPa. After high-temperature testing at 600℃, the strength retention rates were 82% and 78%, respectively, attributed to the formation of intermetallic compounds in the YAG transition layer.

[0135] 4. Abrasion resistance and erosion resistance tests

[0136] 4.1. Test standards: GB / T 12444-2006 "Metallic materials wear test method ring block test" and ASTM G76 "Standard method for solid particle erosion test by gas blasting".

[0137] 4.2. Experimental equipment: Ring block wear tester, gas blasting erosion tester.

[0138] 4.3. Experimental Procedure and Data:

[0139] 4.3.1. Volumetric wear:

[0140] The material was tested for 2 hours on a ring-block testing machine with a load of 20 N, a rotation speed of 150 r / min, and quartz sand (150 mesh) as the abrasive. The volumetric wear of this material was 0.007 cm³. 3 The control sample, Al2O3 ceramic, had a thickness of 0.045 cm. 3 High-chromium cast iron has a thickness of 0.12 cm. 3 .

[0141] 4.3.2. Erosion rate:

[0142] The sample surface was impacted for 1 hour by gas blasting, with SiC particles (100 mesh) sprayed at a speed of 120 m / s and an angle of attack of 90°. The erosion rate of this material was 8 mg / kg, exhibiting excellent resistance to microjet erosion, which is attributed to the high-hardness ceramic phase on the surface and the underlying energy dissipation network.

[0143] 5. Thermophysical properties and dimensional stability testing

[0144] 5.1. Test standard: GB / T 4339-2008 "Determination of thermal expansion characteristic parameters of metallic materials".

[0145] 5.2. Experimental equipment: Thermal expansion apparatus (DIL).

[0146] 5.3. Experimental Procedure and Data:

[0147] 5.3.1. Coefficient of Thermal Expansion (CTE): Tested in the range of 25-600℃. The CTE of the ceramic side of the material is 8.1 × 10⁻⁶. -6 / K, 12.0×10 on the metal side -6 / K exhibits a perfect gradient transition.

[0148] 5.3.2. Verification of the "Zero Expansion Window": Within the critical temperature range of 100-300℃, due to the synergistic effect of the negative expansion effect of ZrW2O8 and the endothermic phase transition of paraffin, the instantaneous CTE of the material is suppressed to 0.5×10⁻⁶. -6 / K to 1.2×10 -6 Between / K, near-zero expansion is achieved, greatly reducing thermal mismatch stress.

[0149] 6. Functional verification experiment

[0150] 6.1. Testing Standards: Refer to the relevant functional material testing methods.

[0151] 6.2. Experimental equipment: fatigue testing machine, ultraviolet lamp, digital microscope, infrared thermal imager, four-probe resistance tester.

[0152] 6.3. Experimental Procedure and Data:

[0153] 6.3.1. Damage Visualization: The sample was subjected to three-point bending until a microcrack (≈10 μm) was generated. Under ambient sunlight, the crack path immediately exhibited bright red fluorescent stripes (Eu). 3+ (Launch), enabling visual positioning without the need for specialized equipment.

[0154] 6.3.2. Self-healing efficiency assessment:

[0155] Chemical repair: A 20 μm wide crack was pre-fabricated and left at room temperature for 24 hours. The flexural strength was measured to recover to 94% of the original value.

[0156] Physical repair (Joule thermal triggering): A 50 μm wide crack was pre-fabricated, and a 5 V voltage was applied to the built-in conductive network for 3 seconds. Infrared thermal imaging showed that the local temperature of the crack rose to 110℃. After cooling, the crack width closed to <5 μm, and it was reloaded to failure, with a strength recovery rate of 88%.

[0157] 6.3.3. Conductive Networks and Self-Monitoring:

[0158] The initial volume resistivity of the material is 0.5 Ω·cm. During fatigue testing, the resistance increases in a stepwise manner as micro-damage accumulates. When the relative rate of change of resistance ΔR / R0 exceeds 5%, it can be used as a damage warning threshold. This time point is approximately 30% of the cycle time before the macro-crack becomes visible.

[0159] Table 1

[0160] Performance indicators This invention's joint material Traditional ceramic adhesive High-performance metal ceramics Bending strength (25℃) 345 MPa 80-120 MPa 180-250 MPa <![CDATA[Fracture toughness K IC > <![CDATA[14.2 MPa·m 1 / 2 ]]> <![CDATA[3-5 MPa·m 1 / 2 ]]> <![CDATA[8-10 MPa·m 1 / 2 ]]> Interfacial shear strength 58-62 MPa 15-25 MPa 30-45 MPa Volumetric wear <![CDATA[0.007 cm 3 ]]> <![CDATA[0.02-0.04 cm 3 ]]> <![CDATA[0.01-0.015 cm 3 ]]> Strength retention rate after 100 thermal cycles (-40-600℃) ≥95% Normal failure 60-80% Crack self-healing efficiency (≤20μm) 94% not applicable not applicable Maximum CTE in the 100-300℃ range <![CDATA[1.2×10 -6 / K]]> <![CDATA[10-15×10 -6 / K]]> <![CDATA[8-12×10 -6 / K]]>

[0161] Table 1 demonstrates that the joint material of this invention comprehensively surpasses existing technologies. Its unique multi-phase change synergistic toughening mechanism, multi-level biomimetic gradient interface, and integrated response function not only solve the contradiction of traditional splicing joints in achieving both strength, toughness, wear resistance, and thermal matching, but also endow the material with self-warning, self-repair, and excellent environmental adaptability in the face of damage. Experimental data fully confirms that this material can revolutionarily transform the "hard connection" of ceramic linings into a "rigid-flexible and vital intelligent connection," providing a breakthrough solution for the long-life and high-reliability operation of equipment such as slurry pumps under extreme working conditions.

[0162] In the description of this invention, it should be noted that, unless otherwise explicitly specified and limited, the terms "installation," "connection," and "linking" should be interpreted broadly. For example, they can refer to a fixed connection, a detachable connection, or an integral connection; they can refer to a mechanical connection or an electrical connection; they can refer to a direct connection or an indirect connection through an intermediate medium; and they can refer to the internal connection of two components. Those skilled in the art will understand the specific meaning of the above terms in this invention based on the specific circumstances.

[0163] The preferred embodiments of the present invention have been described in detail above. However, the present invention is not limited to the above embodiments. Within the scope of knowledge possessed by those skilled in the art, various changes can be made without departing from the spirit of the present invention.

Claims

1. A slurry pump body with an internally lined composite ceramic volute, comprising a slurry pump casing with a discharge pipe, wherein an internal lining layer is laid inside the slurry pump casing, the internal lining layer comprising multiple internal lining splicing blocks 1, the multiple internal lining splicing blocks 1 being arranged in a ring array inside the slurry pump casing, and the multiple internal lining splicing blocks 1 being connected to each other through internal lining splicing blocks 2; characterized in that, Both the inner lining splicing block one and the inner lining splicing block two are arc-shaped. The inner lining splicing block one includes a splicing block body one. An L-shaped connecting groove one is opened on the inner side of one end of the splicing block body one, and an oblique slot one is opened on the inner side of the other end. The inner lining splicing block two includes a splicing block body two. An L-shaped connecting groove two is opened on the outer side of one end of the splicing block body two, and an oblique slot two is opened on the outer side of the other end. The slanted slot 1 of one inner lining splicing block and the slanted slot 2 at one end of one inner lining splicing block 2 are engaged together at an angle, and the L-shaped connecting groove 1 of another inner lining splicing block and the L-shaped connecting groove 2 at the other end of the inner lining splicing block 2 are engaged together at an offset. The snap-fitting units of Angled Slot 1 and Angled Slot 2 are located behind the snap-fitting units of L-shaped Connecting Slot 1 and L-shaped Connecting Slot 2. The inclination of Angled Slot 1 and Angled Slot 2 when snap-fitting is the same as the fluid flow direction inside the slurry pump casing.

2. The slurry pump body with an inner-lined spliced ​​composite ceramic volute according to claim 1, characterized in that, The inner side of the second splicing block is provided with a protrusion, and a wedge-shaped surface is provided on the protrusion. The wedge-shaped surface is used to interact with the fluid and generate a pushing force on the second splicing block, so as to promote a better engagement between the first and second oblique slots, and a better engagement between the first and second L-shaped connecting grooves.

3. The slurry pump body with an inner-lined spliced ​​composite ceramic volute according to claim 1 or 2, characterized in that, Ceramic lining splicing structures are laid between the inner lining splicing block one and the inner lining splicing block two and the slurry pump casing, between the inclined slot one and the inclined slot two, and between the L-shaped connecting slot one and the L-shaped connecting slot two. The ceramic lining splicing structure includes a ceramic lining, a metal substrate, and joint material filling the gaps between them.

4. The slurry pump body with an inner-lined spliced ​​composite ceramic volute according to claim 3, characterized in that, The joint material is a metal-ceramic composite material with multi-stable phase transformation capability and biomimetic gradient topology. Its cured body includes a multi-stable composite matrix, a five-level biomimetic gradient interface system, and an integrated response unit.

5. The slurry pump body with an inner-lined spliced ​​composite ceramic volute according to claim 4, characterized in that, The multistable composite matrix is ​​a bicontinuous three-dimensional interpenetrating network formed by shape memory alloy powder, stainless steel powder and nano-oxide ceramic powder through spark plasma sintering. The volume fraction of the metal phase is 55%-65% and the ceramic phase is 35%-45%. The multistable composite matrix has at least two stable states that can be converted to each other by temperature or stress triggering, corresponding to the high stiffness state, high toughness state and high damping state, respectively. The five-level biomimetic gradient interface system includes a self-assembled monolayer bridge at the metal / ceramic phase interface, a nano-anchoring formed by carbon nanotube arrays grown from the surface of ceramic particles, a SiC whisker layer with gradient orientation controlled by a magnetic field, a mesoscopic transition layer composed of gradient-distributed micropores and hollow ceramic microspheres, and a hyperbolic paraboloid macroscopic geometric topology. The integrated response unit includes fluorescent rare earth complex microcapsules for damage visualization and early warning, a dual-channel self-healing system comprising chemical repair microcapsules and shape memory alloy physical repair based on Joule heating effect, and a thermal expansion intelligent management unit composed of negative thermal expansion material microregions and phase change microcapsules. The chemical composition, porosity, reinforcing phase orientation, thermal expansion coefficient, and functional unit concentration of the joint material in the thickness direction all exhibit a continuous nonlinear gradient change. Furthermore, this gradient distribution is designed for specific ceramic-metal systems through finite element analysis and machine learning optimization algorithms to minimize multi-physics stress during service.

6. The slurry pump body with an inner-lined spliced ​​composite ceramic volute according to claim 5, characterized in that, In the multistable composite matrix, the shape memory alloy powder is Ni. 47 Ti 44 Nb9 (at.%) powder, austenite finishing temperature Af of 70℃±5℃, particle size 0.5-2 μm; stainless steel powder 316L, particle size 1-3 μm; nano-oxide ceramics are a mixture of 3mol% Y2O3-stabilized ZrO2 and α-Al2O3, with average particle sizes of 30-50 nm and 100-200 nm, respectively, and a molar ratio of 7:3; the spark plasma sintering process parameters are: sintering temperature 1250-1350℃, pressure 60-80 MPa, holding time 5-8 min, heating rate 100-200 ℃ / min.

7. The slurry pump body with an inner-lined spliced ​​composite ceramic volute according to claim 5, characterized in that, The five-level biomimetic gradient interface system: The self-assembled monolayer is 12-octadecylphosphonic acid, in which the phosphonic acid groups are bonded to the ceramic phase surface and the alkyl chains are bonded to the metal phase surface. The carbon nanotube array consists of multi-walled carbon nanotubes grown in situ on the surface of ceramic particles via chemical vapor deposition. These nanotubes have a diameter of 10-20 nm, a length of 200-500 nm, and an areal density of 20-40 nanotubes / μm. 2 ; The orientation gradient of SiC whiskers is as follows: in the first surface region, which is 0-30% thick near the ceramic liner, the long axis of the whiskers is parallel to the surface; in the transition region, which is 30-70% thick, the long axis of the whiskers is staggered with the surface normal at 45°±10°; and in the second surface region, which is 70-100% thick near the metal matrix, the long axis of the whiskers is perpendicular to the surface. The equation for the macroscopic geometric topology of a hyperbolic paraboloid is: z = x² / a² - y² / b², where the values ​​of a and b are designed according to the joint width and depth, and the a / b ratio is between 1.5 and 3.

0.

8. The slurry pump body with an inner-lined spliced ​​composite ceramic volute according to claim 5, characterized in that, In the integrated response unit: The wall material of the fluorescent rare earth complex microcapsules is polymethyl methacrylate, with a particle size of 5-15 μm. They contain a mixture of Eu(TTA)3Phen and Tb(AA)3Phen complexes. Under ultraviolet light excitation, they emit red light at 614 nm and green light at 545 nm, respectively. The fluorescence intensity increases more than 10 times after the microcapsules rupture. The chemical repair microcapsules contain active components of terminal vinyl siloxane prepolymer and platinum catalyst microcapsules. The repair agent can be cured within 30 minutes after release and can repair cracks with a width of no more than 20 μm. The physical repair system based on the Joule heating effect includes a three-dimensional conductive network of graphene / carbon nanotubes pre-embedded in the material. The network has a volume resistivity of 0.1-1 Ω·cm. Applying a 5-10 V pulse voltage for 1-5 s can generate a local temperature rise of 100-150℃, which activates the phase transition recovery of the shape memory alloy. The negative thermal expansion material micro-regions are ZrW2O8 with a particle size of 2-5 μm and a volume fraction of 5-10%. The phase change microcapsules have a paraffin / urea-formaldehyde resin core-shell structure and a phase change temperature range of 60-120℃.

9. The slurry pump body with an inner-lined spliced ​​composite ceramic volute according to claim 3, characterized in that, The ceramic lining is made of Al2O3, SiC or ZrO2 ceramic, with a thickness of 5-30 mm and a surface roughness Ra=1.6-3.2μm; The metal matrix is ​​carbon steel, stainless steel, nickel-based high-temperature alloy or titanium alloy, with a thickness of not less than 10 mm; The joint material fills a gap with a width of 0.3-5mm, and the thickness gradient structure matches the properties of the materials on both sides, with no abrupt changes at the interface; Within the joint material layer of the splicing structure, a miniature wireless temperature / strain sensor node is pre-embedded every 50-100 mm along the length direction for real-time monitoring of service status.

10. The slurry pump body with an inner-lined spliced ​​composite ceramic volute according to claim 9, characterized in that, At the interface between the joint material layer and the ceramic liner, a 0.5-2 μm thick zirconium aluminum composite oxide solid solution transition layer is formed by atomic diffusion. At the interface with the metal matrix, a 1-3 μm thick Fe-Ti or Ni-Ti intermetallic compound transition layer is formed. The presence of the transition layer enables the interfacial shear strength to reach 50-65 MPa at room temperature and 35-45 MPa at 600℃.

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