CN104190935A - Manufacturing method for porous powder sintered body and preloading molded body for manufacturing sintered body - Google Patents
Manufacturing method for porous powder sintered body and preloading molded body for manufacturing sintered body Download PDFInfo
- Publication number
- CN104190935A CN104190935A CN201410437077.5A CN201410437077A CN104190935A CN 104190935 A CN104190935 A CN 104190935A CN 201410437077 A CN201410437077 A CN 201410437077A CN 104190935 A CN104190935 A CN 104190935A
- Authority
- CN
- China
- Prior art keywords
- powder
- nickel powder
- sintering
- granularity
- nickel
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Landscapes
- Powder Metallurgy (AREA)
Abstract
The invention discloses a manufacturing method for a porous powder sintered body and a preloading molded body for manufacturing the sintered body. According to the method, the aperture size of the porous powder sintered body can be controlled easily and effectively, and the breakage probability of the molded body during compression molding can be lowered. The method comprises the steps of material preparation, molding and sintering. During material preparation, according to basic raw material powder for manufacturing the porous body, first powder and second powder are used, wherein the first powder and the second powder are different in shape and size, compared with the second powder, the granularity of the first powder is smaller, the compactibility of the first powder during molding is better, and the first powder accounts for 10 percent-90 percent of the total mass of the basic raw material powder. The first powder has the characteristics of being better in compactibility and smaller in sintered aperture size, the second powder has the characteristic of being larger in sintered aperture size, in this way, after the first powder is fully mixed with the second powder, gaps formed in the second powder can be filled with the first powder, on one hand, the effect of controlling the aperture size of the sintered material is achieved, and on the other hand, the compactibility of the mixed powder is improved.
Description
Technical field
The present invention relates to the preparation method of powder sintered porous body and prepare the pre-molding body of this sintered body.
Background technology
Applicant at present to the research emphasis of powder sintered porous filter material concentrate on expansion, the material property of material application improvement, pore-forming mechanism probe into several aspects such as the optimization with preparation technology.In the expansion of sintered porous filtering material application, courageously propose to develop the chemical stability (as corrosion resistance) that can correspondingly meet under this applied environment and require and have for some specific and harsher applied environments the new material of good strainability.Its meaning is, if once such new material is succeeded in developing, just secondary filter technology can be brought into corresponding field, change thus the conventional process flow in this field, its result is very big improvement and long-term economic benefit and the lifting of social benefit of environmental pollution often.But; in the development process of new material; except to the research of material composition, usually also can face the problems in sintered porousization process, for example: after sintering densification, sintering, the excessive permeance property, material aperture of affecting of material tortuosity is difficult to control etc.Therefore, a kind of successful exploitation of new material often can the corresponding innovation relating at aspects such as pore-forming mechanism, preparation technologies.
Summary of the invention
The present invention aims to provide the preparation method of several powder sintered porous filtering alloy, these alloys that show excellent chemical stability and good strainability for particular filter system (referring to the substance system that thing to be filtered forms, can be liquid system or gas system) and prepares the pre-molding body of this alloy.
The powder sintered porous filtering alloy of the first of the present invention, it is made up of 26～30% Mo by mass percentage, 0～2% Fe, 0～0.1% Cr, 0～0.02% C, 0～0.1% Si, 0～1% Mn, 0～5% Al, 0～1.5% Ti and the Ni of surplus; Its average pore size is not more than 20 μ m and relative coefficient of permeability is not less than 0.2m when the liquid filtering
3/ m
2kpah, its average pore size is not more than 60 μ m and relative permeability is not less than 80m when the gas filtration
3/ m
2kpah.It should be explained that, above-mentioned term " be substantially by ... institute form ", concrete meaning in the present invention refers to: this powder sintered porous filtering alloy can only be made up of above-mentioned these elements; Also can on the basis that mainly comprises described element, add element other trace, that can obviously not change alloy property, such as Nb, V, W, Y, Ta, Zr, Co etc.And will in detailed description of the invention, illustrate about the concrete meaning of " relative coefficient of permeability " and " relative permeability ".
The feature of the powder sintered porous filtering alloy of above-mentioned the first is: first, this powder sintered porous filtering alloy needle (is that non-oxidative ion exists, as Fe to complete reduction system
3+, Cu
2+deng) corrosion resistance is very superior; Secondly, the corrosion of any temperature, any concentration hydrochloric acid under ability normal pressure; In addition, in organic acid, bromic acid and the hydrogen chloride gas such as the non-oxidizable sulfuric acid of the intermediate concentration of not inflating, various concentration phosphoric acid, high temperature acetic acid, formic acid, all there is good corrosion resisting property; Also the corrosion of the catalyst of resistance to halogen family in addition.The powder sintered porous filtering alloy ratio of described the first is applicable to oil, the chemical process of multiple harshness, and the distillation of example hydrochloric acid is concentrated; In the production process such as alkylation and low-pressure carbonyl synthesized acetate of ethylbenzene.
In the powder sintered porous filtering alloy of above-mentioned the first, Cr, C, Si, Mn, Al, Ti are selectable components.Wherein Cr, C, Si, Mn can add to put forward heavy alloyed chemical stability according to the concrete residing filtration system of alloy.The major significance of Al can fall low-alloyed tortuosity after being to add to a certain extent.In the time that alloy can meet filtration and infiltration requirement, can not add Al; But in the situation that adding Al, because Al in the high-temperature sintering process of preparing alloy can change liquid phase into and then promote flowing of powder particle, thereby the duct that sintering is formed is more round and smooth, falls thus low-alloyed tortuosity.For improving the object of filtration and infiltration, the quality percentage composition of described Al element is preferably 1～5%, also can be more preferably 3～5%.In addition, can put forward heavy alloyed high temperature hot strength adding of Ti.For example, may be preferably 0.2～1% by the quality percentage composition of (high temperature air filtration of 300～800 DEG C) Ti element when the high temperature filtration system, more preferably 0.5～1%.
The preparation method of the powder sintered porous filtering alloy of above-mentioned the first, its step comprises: 1) each element powder is mixed according to the ratio of above-mentioned setting, wherein Ni powder uses the first nickel powder and the second nickel powder, described the first nickel powder is strip, described the second nickel powder is spherical or near-spherical, described the first nickel powder is 1:(1.2～5 with the ratio of the granularity of the second nickel powder), and add in 10～90% the ratio that the first nickel powder accounts for Ni powder gross mass; 2) above-mentioned mixed powder is carried out successively to granulation, dry and pressure forming, baking temperature is set as to 40～60 DEG C, be set as 4～8 hours drying time, then carry out pressure forming, when pressure forming, pressurize 20～80 seconds under 120～200MPa briquetting pressure, obtains pre-molding body after pressure forming; 3) pre-molding body is carried out to sintering, process at least comprises following two stages: the degreasing stage: sintering temperature rises to 350～450 DEG C from room temperature, and be incubated 60～300 minutes; The high temperature sintering stage: sintering temperature is risen to 1050～1280 DEG C, and be incubated 60～180 minutes; Cooling this porous filtering alloy that obtains.In said method, when preparation is as the powder sintered porous filtering alloy of liquid filtering, can preferably adopt stearic acid when granulation is granulating agent, and stearic addition is 2～8% of mixed powder gross mass; When preparation is as the powder sintered porous filtering alloy of gas filtration, can preferably adopt urea when granulation is granulating agent, and the addition of urea is 5～20% of mixed powder gross mass.In addition, also 1:(2～4 more preferably of the ratio of described the first nickel powder and the granularity of the second nickel powder).Also 120～150MPa more preferably of briquetting pressure when pressure forming.
Formed body rhegma problem when above-mentioned preparation method can be good at avoiding sintering densification problem and pressure forming, and can control effectively to material aperture.First, the method creativeness divides the raw meal (Ni powder) of the infrastructure elements Ni that forms alloy for the first nickel powder and the second nickel powder, wherein the first nickel powder is strip, the second nickel powder is spherical or near-spherical, the first nickel powder is 1:(1.2～5 with the ratio of the granularity of the second nickel powder) (being preferably 1:(2～4)), and the first nickel powder accounts for 10～90% of Ni powder gross mass, like this, because the first nickel powder is the strip nickel powder that granularity is less, there is better (formed body is difficult for rhegma) of briquettability, the feature that sintering back aperture is less, and the second nickel powder larger spherical or near-spherical nickel powder that is granularity, there is briquettability poor (the easy rhegma of formed body), the feature that sintering back aperture is larger, after above-mentioned the first nickel powder is fully mixed with the second nickel powder, the first nickel powder can be filled in the space forming between the second nickel powder, play on the one hand and control the effect in material aperture after sintering (pore diameter range is as required adjusted the ratio of the first nickel powder, for example 30%, 50%, 70%), improve on the one hand the mixed powder briquettability of mixed powder, formed body rhegma probability while reducing pressure forming, in addition, the first nickel powder granularity increases the overall activity of Ni powder compared with I, thereby reduces sintering temperature, promotes the mobile and growth of crystal grain in Powder during Sintering Process, and prevents to a certain extent sintering densification.Secondly, further optimize the briquettability for specific blend powder by the selection of pressure forming parameter, further improved the qualification rate of pressure forming.And according to material composition, when the high temperature sintering stage rises to sintering temperature 1050～1280 DEG C and the special setting that is incubated 60～180 minutes and can ensure sintering, the generation of a small amount of liquid phase, has well avoided sintering densification problem.
Implement the pre-molding body for the preparation of powder sintered porous filtering alloy obtaining in the process of said method, form Ni powder in the powder particle of this pre-molding body and use the first nickel powder and the second nickel powder, described the first nickel powder is strip, described the second nickel powder is spherical or near-spherical, described the first nickel powder is 1:(1.2～5 with the ratio of the granularity of the second nickel powder), and the first nickel powder accounts for 10～90% of Ni powder gross mass.More preferably 1:(2～4 of ratio of described the first nickel powder and the granularity of the second nickel powder).
The powder sintered porous filtering alloy of the second of the present invention, it is to be made up of 14～17% Cr by mass percentage, 15～17% Mo, 0～7% Fe, 0～4.5% W, 0～2.5% Co, 0～0.08% C, 0～1% Si, 0～1% Mn, 0～0.35% V, 0～0.04% P, 0～0.03% S, 0～5% Al, 0～1.5% Ti and the Ni of surplus substantially; Its average pore size is not more than 20 μ m and relative coefficient of permeability is not less than 0.2m when the liquid filtering
3/ m
2kpah, its average pore size is not more than 60 μ m and relative permeability is not less than 80m when the gas filtration
3/ m
2kpah.Above-mentioned term " be substantially by ... form " concrete meaning refer to: this powder sintered porous filtering alloy can only be made up of above-mentioned these elements; Also can on the basis that mainly comprises described element, add element other trace, that can obviously not change alloy property, such as Nb, Y, Ta, Zr etc.
The feature of the powder sintered porous filtering alloy of above-mentioned the second is: first, this powder sintered porous filtering alloy, in oxidisability and reproducibility system, all shows superior rotproofness; Secondly, main moisture-proof chlorine, various oxidisability chloride, chlorate solution, sulfuric acid and oxidisability salt; In addition, in low temperature and middle thermohaline acid, all there is good corrosion resisting property.Therefore, this powder sintered porous filtering alloy ratio is adapted at the industrial circle application such as chemical industry, petrochemical industry, flue gas desulfurization, paper pulp and papermaking, environmental protection.
In the powder sintered porous filtering alloy of above-mentioned the second, Fe, Co, W, C, Si, Mn, V, P, S, Al, Ti are selectable components.Wherein Co, C, Si, Mn, V, P, S can add to put forward heavy alloyed chemical stability according to the concrete residing filtration system of alloy.The quality percentage composition of W can be more preferably 3～4.5%, can improve like this resistance to reduction dielectric corrosion, as local spot corrosion, crevice corrosion; The quality percentage composition of Fe can be more preferably 4～7%.The major significance of Al can fall low-alloyed tortuosity after being to add to a certain extent.In the time that alloy can meet filtration and infiltration requirement, can not add Al; But in the situation that adding Al, because Al in the high-temperature sintering process of preparing alloy can change liquid phase into and then promote flowing of powder particle, thereby the duct that sintering is formed is more round and smooth, falls thus low-alloyed tortuosity.For improving the object of filtration and infiltration, the quality percentage composition of described Al element is preferably 1～5%, also can be more preferably 3～5%.In addition, can put forward heavy alloyed high temperature hot strength adding of Ti.May be preferably 0.2～1% by the quality percentage composition of Ti element when the high temperature filtration system, more preferably 0.5～1%.
The preparation method of the powder sintered porous filtering alloy of above-mentioned the second, its step comprises: 1) each element powder is mixed according to the ratio of above-mentioned setting, wherein Ni powder uses the first nickel powder and the second nickel powder, described the first nickel powder is strip, described the second nickel powder is spherical or near-spherical, described the first nickel powder is 1:(1.2～5 with the ratio of the granularity of the second nickel powder), and add in 10～90% the ratio that the first nickel powder accounts for Ni powder gross mass; 2) above-mentioned mixed powder is carried out successively to granulation, dry and pressure forming, baking temperature is set as to 40～60 DEG C, be set as 4～8 hours drying time, then carry out pressure forming, when pressure forming, pressurize 20～80 seconds under 120～200MPa briquetting pressure, obtains pre-molding body after pressure forming; 3) pre-molding body is carried out to sintering, process at least comprises following two stages: the degreasing stage: sintering temperature rises to 350～450 DEG C from room temperature, and be incubated 60～300 minutes; The high temperature sintering stage: sintering temperature is risen to 1150～1280 DEG C, and be incubated 60～180 minutes; Cooling this porous filtering alloy that obtains.In said method, when preparation is as the powder sintered porous filtering alloy of liquid filtering, can preferably adopt stearic acid when granulation is granulating agent, and stearic addition is 2～8% of mixed powder gross mass; When preparation is as the powder sintered porous filtering alloy of gas filtration, can preferably adopt urea when granulation is granulating agent, and the addition of urea is 5～20% of mixed powder gross mass.In addition, also 1:(2～4 more preferably of the ratio of described the first nickel powder and the granularity of the second nickel powder).More preferably 120～150MPa of briquetting pressure when pressure forming.
Formed body rhegma problem when above-mentioned preparation method can be good at avoiding sintering densification and pressure forming, and can control effectively to material aperture.First, the method creativeness divides the raw meal (Ni powder) of the infrastructure elements Ni that forms alloy for the first nickel powder and the second nickel powder, the first nickel powder is strip, the second nickel powder is spherical or near-spherical, the first nickel powder is 1:(1.2～5 with the ratio of the granularity of the second nickel powder), and the first nickel powder accounts for 10～90% of Ni powder gross mass, like this, because the first nickel powder is the strip nickel powder that granularity is less, there is briquettability better, the feature that sintering back aperture is less, and the second nickel powder larger spherical or near-spherical nickel powder that is granularity, there is briquettability poor, the feature that sintering back aperture is larger, after above-mentioned the first nickel powder is fully mixed with the second nickel powder, the first nickel powder can be filled in the space forming between the second nickel powder, play on the one hand the effect (ratio of aperture adjustment the first nickel powder as required of controlling material aperture after sintering, for example 30%, 50%, 70%), improve on the one hand the mixed powder briquettability of mixed powder, formed body rhegma probability while reducing pressure forming, in addition, the first nickel powder granularity increases the overall activity of Ni powder compared with I, thereby reduction sintering temperature, promote the mobile and growth of crystal grain in Powder during Sintering Process, and prevent to a certain extent sintering densification.Secondly, further optimize the briquettability for specific blend powder by the selection of pressure forming parameter, further improved the qualification rate of pressure forming.And according to material composition, sintering temperature is risen to 1150～1280 DEG C and be incubated the special setting of 60～180 minutes by the high temperature sintering stage, well avoided sintering densification problem.
Implement the pre-molding body for the preparation of powder sintered porous filtering alloy obtaining in the process of said method, form Ni powder in the powder particle of this pre-molding body and use the first nickel powder and the second nickel powder, described the first nickel powder is strip, described the second nickel powder is spherical or near-spherical, described the first nickel powder is 1:(1.2～5 with the ratio of the granularity of the second nickel powder), and the first nickel powder accounts for 10～90% of Ni powder gross mass.Described the first nickel powder is further 1:(2～4 with the ratio of the granularity of the second nickel powder).
The third powder sintered porous filtering alloy provided by the invention, substantially by 21～23.5% Cr by mass percentage, 6～8% Mo, 18～21% Fe, 0～1.5% W, 0～2.5% Co, 0～0.05% C, 0～1% Si, 0～2% Mn, 0～2.5% Ta or/and Nb, 0～5% Al, 0～1.5% Ti and the Ni of surplus form; Its average pore size is not more than 20 μ m and relative coefficient of permeability is not less than 0.2m when the liquid filtering
3/ m
2kpah, its average pore size is not more than 60 μ m and relative permeability is not less than 80m when the gas filtration
3/ m
2kpah.Above-mentioned term " be substantially by ... form " concrete meaning refer to: this powder sintered porous filtering alloy can only be made up of above-mentioned these elements; Certainly this powder sintered porous filtering alloy also can add element other trace, that can obviously not change alloy property, such as V, Y, Zr etc. on the basis that mainly comprises described element.
The feature of above-mentioned the third powder sintered porous filtering alloy is: this powder sintered porous filtering alloy needle has splendid resistance to strong oxidizing property system; Especially tolerate P-levels acid, sulfuric acid, sulfate etc.
In above-mentioned the third powder sintered porous filtering alloy, W, Co, C, Si, Mn, Ta, Nb, Al, Ti are selectable components.Wherein W, Co, C, Si, Mn, Ta, Nb can add to put forward heavy alloyed chemical stability according to the concrete residing filtration system of alloy.The quality percentage composition of Mn can be more preferably 1.5～2.5%, can obviously reduce like this red brittleness of material; Ta is or/and the quality percentage composition of Nb can be more preferably 1～2%, and the effect that can obviously improve like this material opposing local corrosion improves the heat endurance of material simultaneously.The major significance of Al can fall low-alloyed tortuosity after being to add to a certain extent.In the time that alloy can meet filtration and infiltration requirement, can not add Al; But in the situation that adding Al, because Al in the high-temperature sintering process of preparing alloy can change liquid phase into and then promote flowing of powder particle, thereby the duct that sintering is formed is more round and smooth, falls thus low-alloyed tortuosity.For improving the object of filtration and infiltration, the quality percentage composition of described Al element is preferably 1～5%, also can be more preferably 3～5%.In addition, can put forward heavy alloyed high temperature hot strength adding of Ti.May be preferably 0.2～1% by the quality percentage composition of Ti element when the high temperature filtration system, more preferably 0.5～1%.
The preparation method of above-mentioned the third powder sintered porous filtering alloy, its step comprises: 1) each element powder is mixed according to the ratio of above-mentioned setting, wherein Ni powder uses the first nickel powder and the second nickel powder, described the first nickel powder is strip, described the second nickel powder is spherical or near-spherical, described the first nickel powder is 1:(1.2～5 with the ratio of the granularity of the second nickel powder), and add in 10～90% the ratio that the first nickel powder accounts for Ni powder gross mass; 2) above-mentioned mixed powder is carried out successively to granulation, dry and pressure forming, baking temperature is set as to 40～60 DEG C, be set as 4～8 hours drying time, then carry out pressure forming, when pressure forming, pressurize 20～80 seconds under 120～200MPa briquetting pressure, obtains pre-molding body after pressure forming; 3) pre-molding body is carried out to sintering, process at least comprises following two stages: the degreasing stage: sintering temperature rises to 350～450 DEG C from room temperature, and be incubated 60～300 minutes; The high temperature sintering stage: sintering temperature is risen to 1150～1310 DEG C, and be incubated 60～180 minutes; Cooling this porous filtering alloy that obtains.In said method, when preparation is as the powder sintered porous filtering alloy of liquid filtering, can preferably adopt stearic acid when granulation is granulating agent, and stearic addition is 2～8% of mixed powder gross mass; When preparation is as the powder sintered porous filtering alloy of gas filtration, can preferably adopt urea when granulation is granulating agent, and the addition of urea is 5～20% of mixed powder gross mass.In addition, also 1:(2～4 more preferably of the ratio of described the first nickel powder and the granularity of the second nickel powder).More preferably 120～150MPa of briquetting pressure when pressure forming.
Formed body rhegma problem when above-mentioned preparation method can be good at avoiding sintering densification and pressure forming, and can control effectively to material aperture.First, the method creativeness divides the raw meal (Ni powder) of the infrastructure elements Ni that forms alloy for the first nickel powder and the second nickel powder, the first nickel powder is strip, the second nickel powder is spherical or near-spherical, the first nickel powder is 1:(1.2～5 with the ratio of the granularity of the second nickel powder), and the first nickel powder accounts for 10～90% of Ni powder gross mass, like this, because the first nickel powder is the strip nickel powder that granularity is less, there is briquettability better, the feature that sintering back aperture is less, and the second nickel powder larger spherical or near-spherical nickel powder that is granularity, there is briquettability poor, the feature that sintering back aperture is larger, after above-mentioned the first nickel powder is fully mixed with the second nickel powder, the first nickel powder can be filled in the space forming between the second nickel powder, play on the one hand the effect (ratio of aperture adjustment the first nickel powder as required of controlling material aperture after sintering, for example 30%, 50%, 70%), improve on the one hand the mixed powder briquettability of mixed powder, formed body rhegma probability while reducing pressure forming, in addition, the first nickel powder granularity increases the overall activity of Ni powder compared with I, thereby reduction sintering temperature, promote the mobile and growth of crystal grain in Powder during Sintering Process, and prevent to a certain extent sintering densification.Secondly, further optimize the briquettability for specific blend powder by the selection of pressure forming parameter, further improved the qualification rate of pressure forming.And according to material composition, sintering temperature is risen to 1150～1310 DEG C and be incubated the special setting of 60～180 minutes by the high temperature sintering stage, well avoided sintering densification problem.
Implement the pre-molding body for the preparation of porous filtering alloy obtaining in the process of said method, form Ni powder in the powder particle of this pre-molding body and use the first nickel powder and the second nickel powder, described the first nickel powder is strip, described the second nickel powder is spherical or near-spherical, described the first nickel powder is 1:(1.2～5 with the ratio of the granularity of the second nickel powder), and the first nickel powder accounts for 10～90% of Ni powder gross mass.Described the first nickel powder is further 1:(2～4 with the ratio of the granularity of the second nickel powder).
The 4th kind of powder sintered porous filtering alloy of the present invention, it is to be made up of 14～17% Cr by mass percentage, 6～10% Fe, 0～0.15% C, 0～0.5% Si, 0～1% Mn, 0～0.05% Cu, 0～5% Al, 0～1.5% Ti and the Ni of surplus substantially, and its average pore size is not more than 60 μ m and relative permeability is not less than 80m
3/ m
2kpah.It should be explained that, above-mentioned term " be substantially by ... institute form ", concrete meaning refers to: this powder sintered porous filtering alloy can only be made up of above-mentioned these elements; Also can on the basis that mainly comprises described element, add element other trace, that can obviously not change alloy property, such as Nb, V, W, Y, Ta, Zr, Co etc.
Above-mentioned the 4th kind of powder sintered porous filtering alloy has the characteristic (particularly under hot conditions) of good resistance to chlorine, hydrogen chloride gas corrosion, and the gas solid separation being particularly useful under high temperature chlorine, hydrogen chloride system is filtered.
In above-mentioned the 4th kind of powder sintered porous filtering alloy, C, Si, Mn, Cu, Al, Ti are selectable components.Wherein Cr, C, Si, Mn, Cu can add to put forward heavy alloyed chemical stability according to the concrete residing filtration system of alloy.The major significance of Al can fall low-alloyed tortuosity after being to add to a certain extent.In the time that alloy can meet filtration and infiltration requirement, can not add Al; But in the situation that adding Al, because Al in the high-temperature sintering process of preparing alloy can change liquid phase into and then promote flowing of powder particle, thereby the duct that sintering is formed is more round and smooth, falls thus low-alloyed tortuosity.For improving the object of filtration and infiltration, the quality percentage composition of described Al element is preferably 1～5%, also can be more preferably 3～5%.In addition, can put forward heavy alloyed high temperature hot strength adding of Ti.For example, may be preferably 0.2～1% by the quality percentage composition of (high temperature air filtration of 300～800 DEG C) Ti element when the high temperature filtration system, more preferably 0.5～1%.
The preparation method of above-mentioned the 4th kind of powder sintered porous filtering alloy, its step comprises: 1) each element powder is mixed according to the ratio of above-mentioned setting, wherein Ni powder uses the first nickel powder and the second nickel powder, described the first nickel powder is strip, described the second nickel powder is spherical or near-spherical, described the first nickel powder is 1:(1.2～5 with the ratio of the granularity of the second nickel powder), and add in 10～90% the ratio that the first nickel powder accounts for Ni powder gross mass; 2) above-mentioned mixed powder is carried out successively to granulation, dry and pressure forming, baking temperature is set as to 40～60 DEG C, be set as 4～8 hours drying time, then carry out pressure forming, when pressure forming, pressurize 20～80 seconds under 120～220MPa briquetting pressure, obtains pre-molding body after pressure forming; 3) pre-molding body is carried out to sintering, process at least comprises following two stages: the degreasing stage: sintering temperature rises to 350～450 DEG C from room temperature, and be incubated 60～300 minutes; The high temperature sintering stage: sintering temperature is risen to 1200～1320 DEG C, and be incubated 120～300 minutes; Cooling this porous filtering alloy that obtains.In said method, when granulation, can preferably adopt urea is granulating agent, and the addition of urea is 5～20% of mixed powder gross mass.In addition, also 1:(2～4 more preferably of the ratio of described the first nickel powder and the granularity of the second nickel powder).Also 150～200MPa more preferably of briquetting pressure when pressure forming.
Formed body rhegma problem when above-mentioned preparation method can be good at avoiding pressure forming, and can control effectively to material aperture.First, the method creativeness divides the raw meal (Ni powder) of the infrastructure elements Ni that forms alloy for the first nickel powder and the second nickel powder, wherein the first nickel powder is strip, the second nickel powder is spherical or near-spherical, the first nickel powder is 1:(1.2～5 with the ratio of the granularity of the second nickel powder) (being preferably 1:(2～4)), and the first nickel powder accounts for 10～90% of Ni powder gross mass, like this, because the first nickel powder is the strip nickel powder that granularity is less, there is better (formed body is difficult for rhegma) of briquettability, the feature that sintering back aperture is less, and the second nickel powder larger spherical or near-spherical nickel powder that is granularity, there is briquettability poor (the easy rhegma of formed body), the feature that sintering back aperture is larger, after above-mentioned the first nickel powder is fully mixed with the second nickel powder, the first nickel powder can be filled in the space forming between the second nickel powder, play on the one hand and control the effect in material aperture after sintering (pore diameter range is as required adjusted the ratio of the first nickel powder, for example 30%, 50%, 70%), improve on the one hand the mixed powder briquettability of mixed powder, formed body rhegma probability while reducing pressure forming, in addition, the first nickel powder granularity increases the overall activity of Ni powder compared with I, thereby reduces sintering temperature, promotes the mobile and growth of crystal grain in Powder during Sintering Process, and prevents to a certain extent sintering densification.In addition, further optimize the briquettability for specific blend powder by the selection of pressure forming parameter, further improved the qualification rate of pressure forming.
Implement the pre-molding body for the preparation of powder sintered porous filtering alloy obtaining in the process of said method, form Ni powder in the powder particle of this pre-molding body and use the first nickel powder and the second nickel powder, described the first nickel powder is strip, described the second nickel powder is spherical or near-spherical, described the first nickel powder is 1:(1.2～5 with the ratio of the granularity of the second nickel powder), and the first nickel powder accounts for 10～90% of Ni powder gross mass.More preferably 1:(2～4 of ratio of described the first nickel powder and the granularity of the second nickel powder).The first nickel powder accounts for Ni powder gross mass also can be more preferably 15～50%.
In sum, above the main common ground of four kinds of powder sintered porous filtering alloys be to be Ni base alloy, and all taked special technological means for the raw meal (Ni powder) of the infrastructure elements Ni that forms this alloy in preparation technology.Applicant exploitation above-mentioned first three plant in the process of powder sintered porous filtering alloy, find to have the problems such as sintering densification, material permeability is on the low side, tortuosity is larger by the technique that conventional powder metallurgic method is prepared sintered porous material, thereby its average pore size is not more than 20 μ m and relative coefficient of permeability is not less than 0.2m far cannot reach as liquid filtering time
3/ m
2kpah, its average pore size is not more than 60 μ m and relative permeability is not less than 80m when the gas filtration
3/ m
2the technical requirement of kpah.By above-mentioned series of measures, make obtained powder sintered porous filtering alloy reveal excellent chemical stability for particular filter diagram of system, reach again good strainability simultaneously.In the process of above-mentioned the 4th kind of powder sintered porous filtering alloy of exploitation, sintering densification problem is outstanding, but low qualified while finding pressure forming, the easy rhegma of pre-compaction forming body, after taking the treatment measures of Ni powder, pre-compaction forming body qualification rate can greatly improve.
In addition, also can further summarize and draw a kind of aperture size that can simply effectively control powder sintered porous body by foregoing, and can reduce pressure forming time the powder sintered porous body of formed body rhegma probability preparation method and prepare the pre-molding body of this sintered body.The preparation method who is this powder sintered porous body is: step comprises batching, moulding and sintering, when batching, use shape, the first powder varying in size and the second powder for the basic material powder of this porous body of preparation, briquettability when described the first powder is compared the less and moulding of the second powder granularity is better, and the first powder accounts for 10～90% of this basic material powder gross mass.If porous body is Ni base alloy, the first powder is the first nickel powder, and the second powder is the second nickel powder.Due to the first powder, to have briquettability better, feature that sintering back aperture is less (because of the first powder granularity less), and the second powder have the feature that sintering back aperture is larger (because of the second powder granularity larger), after above-mentioned the first powder is fully mixed with the second powder, the first powder can be filled in the space forming between the second powder, play on the one hand the effect (ratio of aperture adjustment the first powder as required of controlling material aperture after sintering, for example 30%, 50%, 70%), improve on the one hand the briquettability of mixed powder, formed body rhegma probability while reducing pressure forming, in addition, the first powder granularity increases the overall activity of basic material powder compared with I, thereby reduction sintering temperature, promote the mobile and growth of crystal grain in Powder during Sintering Process, and prevent to a certain extent sintering densification.
The preferably concrete mode of one in the preparation method of this powder sintered porous body is: described the first powder is strip, and described the second powder is spherical or near-spherical, and described the first powder is 1:(1.2～5 with the ratio of the granularity of the second powder).The better feature of briquettability when wherein the first powder of strip has moulding, and the accumulation space of the second powder of spherical or near-spherical is larger, sintering porosity is higher; The first powder and the ratio of the granularity of the second powder are set as to 1:(1.2～5), can better guarantee the briquettability of mixed powder and the accuracy that aperture is controlled.Wherein more preferably 1:(2～4 of ratio of the first powder and the granularity of the second powder).In addition, the first powder can adopt electrolytic powder (shape of electrolytic powder is strip), and the second powder can adopt atomized powder (shape of atomized powder is spherical or near-spherical).Certainly, the first powder of strip not can only adopt electrolysis mode to obtain, and also can obtain the first powder of strip by other Preparation Technique of Powders (as oxidation-reduction method); The second powder spherical or near-spherical not can only adopt atomizing type to obtain, and also can obtain the second powder by other known Preparation Technique of Powders.
Implement the pre-molding body for the preparation of powder sintered porous body obtaining in the process of said method, the basic material powder forming in the powder particle of this pre-molding body uses shape, the first powder varying in size and the second powder, briquettability when described the first powder is compared the less and moulding of the second powder granularity is better, and the first powder accounts for 10～90% of this basic material powder gross mass.Wherein, further, described the first powder is strip, and described the second powder is spherical or near-spherical, and described the first powder is 1:(1.2～5 with the ratio of the granularity of the second powder).
Below in conjunction with detailed description of the invention, the present invention will be further described.The aspect that the present invention is additional and advantage in the following description part provide, and part will become obviously from the following description, or recognize by practice of the present invention.
Detailed description of the invention
Preparation method below by four groups of experimental examples to above-mentioned several powder sintered Ni base porous filtering alloys of the present invention and the powder sintered Ni base porous filtering alloy being obtained by these methods are specifically described.By these explanations, those skilled in the art can know the outstanding feature of recognizing that powder sintered Ni base porous filtering alloy of the present invention has.The numbering of the experimental example below relating to is consistent with the numbering of corresponding " sample ".
< battery of tests >
The material composition of the experimental example 1 to 12 of first group of test example and content (by percentage to the quality) are in table 1.Wherein, the powder sintered porous filtering alloy that material applications A refers to preparation is as liquid filtering; Material applications B refers to that the powder sintered porous filtering alloy of preparation is as gas filtration.In the experimental example 1 to 12 of battery of tests, each experimental example also comprises 5 identical examples.
Table 1---material composition and the content of experimental example 1 to 12 in first group of test example
Note: in table, "×" represents no this item.
In above-mentioned experimental example 1 to 12, Ni powder has all used the first nickel powder and the second nickel powder.Wherein, described the first nickel powder is selected the electrolytic nickel powder of strip, and granularity is 10～25 μ m; Described the second nickel powder is chosen as the atomization nickel powder of spherical or near-spherical, and granularity is 35～45 μ m.The particle diameter of all the other raw meal except Ni powder is-400 orders.Above-mentioned particle diameter determines according to design aperture and the pore-size distribution of the standby powder sintered Ni base porous filtering alloy of drawing up, and those skilled in the art can adjust according to the requirement of aperture situation.In addition, in test example 1-4, the first nickel powder accounts for 35% of Ni powder gross mass, and in test example 5-7,9-11, the first nickel powder accounts for 55% of Ni powder gross mass, and in test example 8,12, the first nickel powder accounts for 20% of Ni powder gross mass.
Press table 1 listed, respectively the raw material of experimental example 1 to 12 is mixed.After fully mixing, then the powder of experimental example 1 to 12 is carried out to granulation, after granulation, be dried again, baking temperature is set as 55 DEG C, is set as 6 hours drying time.In test example 1-7,9-11, adopting stearic acid when granulation is granulating agent, and stearic addition is 5% of mixed powder gross mass.Select stearic effect and advantage to be herein: to be 1) agglomerated powder granules, to prevent component segregation, secondly, there is certain lubrication, suppress easy-formation and the easily demoulding; 2) stearic acid easily decomposes, 360-370 DEG C is decomposed completely, and catabolite is CO2, CO, H2O etc., easily overflows noresidue, be granulating agent with adopting urea when granulation in the reactionless test example 8,12 of matrix material, the addition of urea is 12% of mixed powder gross mass.Select effect and the advantage of urea to be herein: 1) as blowing agent, to improve the porosity of material; 2) decomposition temperature low (160 DEG C), and catabolite is ammonia and cyanic acid, after can sending out, leaves position, hole, and forms perforate.
Afterwards, respectively the powder of experimental example 1 to 12 is packed in the isostatic pressing mold of unified specification, then these moulds are placed in respectively to cold isostatic compaction machine, pressurize 60 seconds under 150MPa briquetting pressure, makes the tubulose pre-molding body that is numbered 1 to 12 after the demoulding.Above-mentioned isostatic compaction the results are shown in Table 2.As can be seen from Table 2, only the example 3 of experimental example 12 pre-molding body find rhegma, all the other pre-molding bodies are all without rhegma, isostatic compaction qualification rate is significantly better than existing situation.
Table 2---isostatic compaction qualification rate
| Experimental example numbering | Example 1 | Example 2 | Example 3 | Example 4 | Example 5 |
| 1 | √ | √ | √ | √ | √ |
| 2 | √ | √ | √ | √ | √ |
| 3 | √ | √ | √ | √ | √ |
| 4 | √ | √ | √ | √ | √ |
| 5 | √ | √ | √ | √ | √ |
| 6 | √ | √ | √ | √ | √ |
| 7 | √ | √ | √ | √ | √ |
| 8 | √ | √ | √ | √ | √ |
| 9 | √ | √ | √ | √ | √ |
| 10 | √ | √ | √ | √ | √ |
| 11 | √ | √ | √ | √ | √ |
| 12 | √ | √ | × | √ | √ |
Note: in table, "×" represents that pre-molding body has rhegma, defective; In table, " √ " represents that pre-molding body is without rhegma, qualified.
Then, choose respectively the pre-molding body of one of them example in experimental example 1 to 12 and pack sintering boat into, then these sintering boats are placed in sintering furnace and carry out sintering, cooling with stove after sintering, finally from each sintering boat, obtain again sample 1 to 12.The sintering schedule of experimental example 1 to 12 all comprises following two stages.First stage is the degreasing stage: sintering temperature rises to 400 DEG C from room temperature, and is incubated 180 minutes; Second stage is the high temperature sintering stage: sintering temperature is risen to 1150 DEG C, and be incubated 120 minutes; Cooling this porous filtering alloy that obtains.
The strainability of sample 1 to 12 is tested as table 3.Wherein, the mensuration of material porosity and average pore size adopts bubble method; Relative coefficient of permeability is specially in every square metre of filter area, every kpa (kPa) filtration pressure difference and per hour under water flux; Relative permeability is specially in every square metre of filter area, every kpa (kPa) filtration pressure difference and per hour under air flux; The test of Tensile strength is to record by stretching-machine after sample 1 to 12 is processed as to standard specimen by CNS GB7963-87.
Table 3---result of the test
Note: in table, "×" represents no this item.
The chemical stability of sample 1 to 12 is tested as table 3.Wherein, erosion test 1 is to characterize at mass fraction soaking at room temperature weight-loss ratio (%) after 60 days in 10% hydrochloric acid solution; Erosion test 2 is to characterize at mass fraction soaking at room temperature weight-loss ratio (%) after 60 days in 80% hydrochloric acid solution; Erosion test 3 is to characterize at mass fraction soaking at room temperature weight-loss ratio (%) after 60 days in 60% phosphoric acid solution; Erosion test 4 is to characterize at mass fraction soaking at room temperature weight-loss ratio (%) after 60 days in 60% sulfuric acid solution; Erosion test 5 is to characterize at mass fraction soaking at room temperature weight-loss ratio (%) after 60 days in 60% formic acid solution; Erosion test 5 to use the weight-loss ratio (%) after 60 days to characterize in hydrogen chloride gas.
Table 4---result of the test
Note: in table, "×" represents no this item.
Second group of test > of <
The material composition of the experimental example 1 to 12 of second group of test and content (by percentage to the quality) are in table 5.Wherein, the powder sintered porous filtering alloy that material applications A refers to preparation is as liquid filtering; Material applications B refers to that the powder sintered porous filtering alloy of preparation is as gas filtration.In the experimental example 1 to 12 of second group of test, each experimental example only has an example.
Table 5---material composition and the content of experimental example 1 to 12 in second group of test example
Note: in table, "×" represents no this item.
In above-mentioned experimental example 1 to 12, Ni powder has all used the first nickel powder and the second nickel powder.Wherein, described the first nickel powder is selected the electrolytic nickel powder of strip, granularity 10～25 μ m; Described the second nickel powder is chosen as the atomization nickel powder of spherical or near-spherical, granularity 35～45 μ m.The particle diameter of all the other raw meal outside Ni powder is-400 orders.Equally, above-mentioned particle diameter determines according to design aperture and the pore-size distribution of the standby powder sintered Ni base porous filtering alloy of drawing up, and those skilled in the art can adjust according to the requirement of aperture situation.In addition, in test example 1-4, the first nickel powder accounts for 35% of Ni powder gross mass, and in test example 5-11, the first nickel powder accounts for 55% of Ni powder gross mass, and in test example 12, the first nickel powder accounts for 20% of Ni powder gross mass.
Press table 5 listed, respectively the raw material of experimental example 1 to 12 is mixed.After fully mixing, then the powder of experimental example 1 to 12 is carried out to granulation, after granulation, be dried again, baking temperature is set as 55 DEG C, is set as 6 hours drying time.In test example 1-11, adopting stearic acid when granulation is granulating agent, and stearic addition is 5% of mixed powder gross mass.In test example 12, adopting urea when granulation is granulating agent, and the addition of urea is 12% of mixed powder gross mass.
Afterwards, respectively the powder of experimental example 1 to 12 is packed in the isostatic pressing mold of unified specification, then these moulds are placed in respectively to cold isostatic compaction machine, pressurize 60 seconds under 150MPa briquetting pressure, makes the tubulose pre-molding body that is numbered 1 to 12 after the demoulding.These pre-molding bodies are all without rhegma.
Then, respectively by the pre-molding body in experimental example 1 to 12 and pack sintering boat into, then these sintering boats are placed in sintering furnace and carry out sintering, cooling with stove after sintering, finally from each sintering boat, obtain again sample 1 to 12.The sintering schedule of experimental example 1 to 12 all comprises following two stages.First stage is the degreasing stage: sintering temperature rises to 400 DEG C from room temperature, and is incubated 180 minutes; Second stage is the high temperature sintering stage: sintering temperature is risen to 1200 DEG C, and be incubated 120 minutes; After cooling, obtain respectively sample 1 to 12.
The strainability of sample 1 to 12 is tested as table 6.Wherein, the mensuration of material porosity and average pore size adopts bubble method; Relative coefficient of permeability is specially in every square metre of filter area, every kpa (kPa) filtration pressure difference and per hour under water flux; Relative permeability is specially in every square metre of filter area, every kpa (kPa) filtration pressure difference and per hour under air flux; The test of Tensile strength is to record by stretching-machine after sample 1 to 12 is processed as to standard specimen by CNS GB7963-87.
Table 6---result of the test
Note: in table, "×" represents no this item.
The chemical stability of sample 1 to 12 is tested as table 7.Wherein, erosion test 1 is to characterize at mass fraction soaking at room temperature weight-loss ratio (%) after 60 days in 10% hydrochloric acid solution; Erosion test 2 is to characterize at mass fraction soaking at room temperature weight-loss ratio (%) after 60 days in 10% sulfuric acid solution; Erosion test 3 is to characterize at mass fraction soaking at room temperature weight-loss ratio (%) after 60 days in 10% sodium chloride solution; Erosion test 4 is to characterize at mass fraction soaking at room temperature weight-loss ratio (%) after 60 days in 10% ferric chloride solution; Erosion test 5 to use the weight-loss ratio (%) after 60 days to characterize in wet chlorine.
Table 7---result of the test
Note: in table, "×" represents no this item.
The 3rd group of test > of <
The material composition of the experimental example 1 to 9 of the 3rd group of test and content (by percentage to the quality) are in table 8.Wherein, the powder sintered porous filtering alloy that material applications A refers to preparation is as liquid filtering; Material applications B refers to that the powder sintered porous filtering alloy of preparation is as gas filtration.In the experimental example 1 to 9 of battery of tests, each experimental example only has an example.
Table 8---material composition and the content of experimental example 1 to 9 in the 3rd group of test example
Note: in table, "×" represents no this item.
In above-mentioned experimental example 1 to 9, Ni powder has all used the first nickel powder and the second nickel powder.Wherein, described the first nickel powder is selected the electrolytic nickel powder of strip, granularity 10～25 μ m; Described the second nickel powder is chosen as the atomization nickel powder of spherical or near-spherical, granularity 35～45 μ m.The particle diameter of all the other raw meal outside Ni powder is-400 orders.In above-mentioned test example 1-8, the first nickel powder accounts for 55% of Ni powder gross mass, and in test example 9, the first nickel powder accounts for 20% of Ni powder gross mass.
Press table 8 listed, respectively the raw material of experimental example 1 to 9 is mixed.After fully mixing, then the powder of experimental example 1 to 9 is carried out to granulation, after granulation, be dried again, baking temperature is set as 55 DEG C, is set as 6 hours drying time.In test example 1-8, adopting stearic acid when granulation is granulating agent, and stearic addition is 5% of mixed powder gross mass.In test example 9, adopting urea when granulation is granulating agent, and the addition of urea is 12% of mixed powder gross mass.
Afterwards, respectively the powder of experimental example 1 to 9 is packed in the isostatic pressing mold of unified specification, then these moulds are placed in respectively to cold isostatic compaction machine, pressurize 60 seconds under 150MPa briquetting pressure, makes the tubulose pre-molding body that is numbered 1 to 9 after the demoulding.These pre-molding bodies are all without rhegma.
Then, by the pre-molding body of experimental example 1 to 9 and pack sintering boat into, then these sintering boats are placed in sintering furnace and carry out sintering, cooling with stove after sintering, finally from each sintering boat, obtain again sample 1 to 9.The sintering schedule of experimental example 1 to 9 all comprises following two stages.First stage is the degreasing stage: sintering temperature rises to 400 DEG C from room temperature, and is incubated 180 minutes; Second stage is the high temperature sintering stage: sintering temperature is risen to 1200 DEG C, and be incubated 120 minutes; After cooling, obtain respectively sample 1 to 9.
The strainability of sample 1 to 9 is tested as table 9.Wherein, the mensuration of material porosity and average pore size adopts bubble method; Relative coefficient of permeability is specially in every square metre of filter area, every kpa (kPa) filtration pressure difference and per hour under water flux; Relative permeability is specially in every square metre of filter area, every kpa (kPa) filtration pressure difference and per hour under air flux; The test of Tensile strength is to record by stretching-machine after sample 1 to 9 is processed as to standard specimen by CNS GB7963-87.
Table 9---result of the test
Note: in table, "×" represents no this item.
The chemical stability of sample 1 to 9 is tested as table 10.Wherein, erosion test 1 is to characterize at mass fraction soaking at room temperature weight-loss ratio (%) after 60 days in 10% phosphoric acid solution; Erosion test 2 is to characterize at mass fraction soaking at room temperature weight-loss ratio (%) after 60 days in 30% phosphoric acid solution; Erosion test 3 is to characterize at mass fraction soaking at room temperature weight-loss ratio (%) after 60 days in 10% sulfuric acid solution; Erosion test 4 is to characterize at mass fraction soaking at room temperature weight-loss ratio (%) after 60 days in 30% sulfuric acid solution; Erosion test 5 to use the weight-loss ratio (%) after 60 days to characterize in dry chlorine gas.
Table 10---result of the test
Note: in table, "×" represents no this item.
The 4th group of experimental example > of <
The material composition of the experimental example 1 to 8 of the 4th group of test and content (by percentage to the quality) are in table 11.Wherein, the powder sintered porous filtering alloy that material applications B refers to preparation is as gas filtration.In the experimental example 1 to 8 of battery of tests, each experimental example only has an example.
Table 11---material composition and the content of experimental example 1 to 8 in the 4th group of test example
Note: in table, "×" represents no this item.
In above-mentioned experimental example 1 to 8, Ni powder has all used the first nickel powder and the second nickel powder.Wherein, described the first nickel powder is selected the electrolytic nickel powder of strip, granularity 10～25 μ m; Described the second nickel powder is chosen as the atomization nickel powder of spherical or near-spherical, granularity 35～45 μ m.The particle diameter of all the other raw meal outside Ni powder is-400 orders.In above-mentioned test example 1-8, the first nickel powder accounts for 20% of Ni powder gross mass.
Press table 11 listed, respectively the raw material of experimental example 1 to 8 is mixed.After fully mixing, then the powder of experimental example 1 to 8 is carried out to granulation, after granulation, be dried again, baking temperature is set as 55 DEG C, is set as 6 hours drying time.In test example 1-8, adopting urea when granulation is granulating agent, and the addition of urea is 12% of mixed powder gross mass.
Afterwards, respectively the powder of experimental example 1 to 8 is packed in the isostatic pressing mold of unified specification, then these moulds are placed in respectively to cold isostatic compaction machine, pressurize 60 seconds under 180MPa briquetting pressure, makes the tubulose pre-molding body that is numbered 1 to 8 after the demoulding.These pre-molding bodies are all without rhegma.
Then, by the pre-molding body of experimental example 1 to 8 and pack sintering boat into, then these sintering boats are placed in sintering furnace and carry out sintering, cooling with stove after sintering, finally from each sintering boat, obtain again sample 1 to 8.The sintering schedule of experimental example 1 to 8 all comprises following two stages.First stage is the degreasing stage: sintering temperature rises to 400 DEG C from room temperature, and is incubated 180 minutes; Second stage is the high temperature sintering stage: sintering temperature is risen to 1300 DEG C, and be incubated 200 minutes; After cooling, obtain respectively sample 1 to 8.
The strainability of sample 1 to 8 is tested as table 12.Wherein, the mensuration of material porosity and average pore size adopts bubble method; Relative coefficient of permeability is specially in every square metre of filter area, every kpa (kPa) filtration pressure difference and per hour under water flux; Relative permeability is specially in every square metre of filter area, every kpa (kPa) filtration pressure difference and per hour under air flux; The test of Tensile strength is to record by stretching-machine after sample 1 to 8 is processed as to standard specimen by CNS GB7963-87.
Table 12---result of the test
Note: in table, "×" represents no this item.
The chemical stability of sample 1 to 8 is tested as table 10.Wherein, erosion test 1 to use the weight-loss ratio (%) after 30 days to characterize under 400 DEG C of dry chlorine gas.
Table 13---result of the test
Note: in table, "×" represents no this item.
Claims (10)
1. the preparation method of powder sintered porous body, step comprises batching, moulding and sintering, it is characterized in that: when batching, use shape, the first powder varying in size and the second powder for the basic material powder of this porous body of preparation, briquettability when described the first powder is compared the less and moulding of the second powder granularity is better, and the first powder accounts for 10～90% of this basic material powder gross mass.
2. the preparation method of powder sintered porous body as claimed in claim 1, is characterized in that: described the first powder is strip, described the second powder is spherical or near-spherical, and described the first powder is 1:(1.2～5 with the ratio of the granularity of the second powder).
3. the preparation method of powder sintered porous body as claimed in claim 2, is characterized in that: described the first powder is 1:(2～4 with the ratio of the granularity of the second powder).
4. the preparation method of powder sintered porous body as claimed in claim 2, is characterized in that: described the first powder is electrolytic powder, described the second powder is atomized powder.
5. the preparation method of powder sintered porous body as described in any one claim in claim 1 to 4, is characterized in that: described porous body is Ni base alloy, and the first powder is the first nickel powder, and the second powder is the second nickel powder.
6. implement the claims the pre-molding body for the preparation of powder sintered porous body obtaining in the process of method described in 1, it is characterized in that: the basic material powder forming in the powder particle of this pre-molding body uses shape, the first powder varying in size and the second powder, briquettability when described the first powder is compared the less and moulding of the second powder granularity is better, and the first powder accounts for 10～90% of this basic material powder gross mass.
7. pre-molding body as claimed in claim 6, is characterized in that: described the first powder is strip, and described the second powder is spherical or near-spherical, and described the first powder is 1:(1.2～5 with the ratio of the granularity of the second powder).
8. pre-molding body as claimed in claim 7, is characterized in that: described the first powder is 1:(2～4 with the ratio of the granularity of the second powder).
9. pre-molding body as claimed in claim 7, is characterized in that: described the first powder is electrolytic powder, and described the second powder is atomized powder.
10. pre-molding body as described in any one claim in claim 6 to 9, is characterized in that: described porous body is Ni base alloy, and the first powder is the first nickel powder, and the second powder is the second nickel powder.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410437077.5A CN104190935B (en) | 2014-08-31 | 2014-08-31 | The preparation method of powder sintered porous body and prepare the pre-molding body of the sintered body |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201410437077.5A CN104190935B (en) | 2014-08-31 | 2014-08-31 | The preparation method of powder sintered porous body and prepare the pre-molding body of the sintered body |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN104190935A true CN104190935A (en) | 2014-12-10 |
| CN104190935B CN104190935B (en) | 2017-06-16 |
Family
ID=52076382
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201410437077.5A Active CN104190935B (en) | 2014-08-31 | 2014-08-31 | The preparation method of powder sintered porous body and prepare the pre-molding body of the sintered body |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN104190935B (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104625071A (en) * | 2015-01-28 | 2015-05-20 | 东莞劲胜精密组件股份有限公司 | Preparation method for powder injection molding surface pore material |
| CN106994512A (en) * | 2017-04-18 | 2017-08-01 | 中南大学 | A kind of composite bore diameter copper sintered porous material and its preparation method and application |
| WO2021037226A1 (en) * | 2019-08-29 | 2021-03-04 | 深圳市中光工业技术研究院 | Fluorescent ceramic, preparation method therefor and light source device |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH07118706A (en) * | 1993-10-26 | 1995-05-09 | Katayama Tokushu Kogyo Kk | Metallic porous body and its production |
| JP2002285204A (en) * | 2001-03-23 | 2002-10-03 | National Institute Of Advanced Industrial & Technology | Method for manufacturing high-strength porous body |
| WO2003008133A1 (en) * | 2001-07-17 | 2003-01-30 | SOUKHOLINSKI-MESTETCHKIN, Sergey Leonidovich | Method for producing porous semiproducts from aluminium alloys powder |
| JP2006509918A (en) * | 2002-12-12 | 2006-03-23 | マイクロリス・コーポレイシヨン | Porous sintered composite material |
| CN102166651A (en) * | 2011-03-29 | 2011-08-31 | 黑龙江科技学院 | Method for manufacturing porous metal parts by laser scanning |
| CN102836997A (en) * | 2011-06-22 | 2012-12-26 | 烟台龙源电力技术股份有限公司 | Metal powder sintered porous body and preparation method thereof |
-
2014
- 2014-08-31 CN CN201410437077.5A patent/CN104190935B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH07118706A (en) * | 1993-10-26 | 1995-05-09 | Katayama Tokushu Kogyo Kk | Metallic porous body and its production |
| JP2002285204A (en) * | 2001-03-23 | 2002-10-03 | National Institute Of Advanced Industrial & Technology | Method for manufacturing high-strength porous body |
| WO2003008133A1 (en) * | 2001-07-17 | 2003-01-30 | SOUKHOLINSKI-MESTETCHKIN, Sergey Leonidovich | Method for producing porous semiproducts from aluminium alloys powder |
| JP2006509918A (en) * | 2002-12-12 | 2006-03-23 | マイクロリス・コーポレイシヨン | Porous sintered composite material |
| CN102166651A (en) * | 2011-03-29 | 2011-08-31 | 黑龙江科技学院 | Method for manufacturing porous metal parts by laser scanning |
| CN102836997A (en) * | 2011-06-22 | 2012-12-26 | 烟台龙源电力技术股份有限公司 | Metal powder sintered porous body and preparation method thereof |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104625071A (en) * | 2015-01-28 | 2015-05-20 | 东莞劲胜精密组件股份有限公司 | Preparation method for powder injection molding surface pore material |
| CN106994512A (en) * | 2017-04-18 | 2017-08-01 | 中南大学 | A kind of composite bore diameter copper sintered porous material and its preparation method and application |
| WO2021037226A1 (en) * | 2019-08-29 | 2021-03-04 | 深圳市中光工业技术研究院 | Fluorescent ceramic, preparation method therefor and light source device |
| CN112441817A (en) * | 2019-08-29 | 2021-03-05 | 深圳市中光工业技术研究院 | Fluorescent ceramic, preparation method thereof and light source device |
| JP2022552054A (en) * | 2019-08-29 | 2022-12-15 | シェンチェン ライティング インスティテュート | Fluorescent ceramics, manufacturing method thereof, and light source device |
| CN112441817B (en) * | 2019-08-29 | 2023-12-29 | 深圳市绎立锐光科技开发有限公司 | Fluorescent ceramic, preparation method thereof and light source device |
| JP7450701B2 (en) | 2019-08-29 | 2024-03-15 | 深▲せん▼市繹立鋭光科技開発有限公司 | Fluorescent ceramics and their manufacturing method, light source device |
Also Published As
| Publication number | Publication date |
|---|---|
| CN104190935B (en) | 2017-06-16 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN104195374A (en) | Powder sintered porous filter alloy, preparation method thereof and pre-compression molded body | |
| CN104190918A (en) | Powder sintering porous filter alloy, preparation method thereof and pre-pressing molding body for preparing powder sintering porous filter alloy | |
| CN103397256B (en) | The sintering Fe-Al base alloy porous material of resistance to high temperature oxidation and filtering element | |
| CN103343251B (en) | Sintering Ti-Al base alloy porous material, application and improve the method for its pore structure | |
| CN103215470B (en) | The preparation method of the open celled foam copper that a kind of pore structure parameter is controlled | |
| CN101358304A (en) | NiAl intermetallic compound porous material and preparation method thereof | |
| CN103409678B (en) | Sintering Fe-Al base alloy porous material and apply its filtering element | |
| CN102828096B (en) | Metal ceramic cutting tool material and preparation method thereof | |
| CN103290248B (en) | A kind of particle reinforce abradable porous titanium preparation method | |
| CN104419841A (en) | Preparation method of powdery sintered metal porous body | |
| CN104190935A (en) | Manufacturing method for porous powder sintered body and preloading molded body for manufacturing sintered body | |
| CN103397243B (en) | The preparation method of sintering Fe-Al base alloy porous material | |
| CN103014507A (en) | Powder metallurgy flange and preparation method thereof | |
| CN106191505B (en) | Preparation method of high-temperature oxidation-resistant porous material | |
| US10077214B2 (en) | Sintered porous material and filter element using same | |
| CN104233004B (en) | Powder sintered porous filtering alloy, its preparation method and its pre-molding body | |
| CN106987740A (en) | A kind of porous aluminum based composite metal material and preparation method thereof | |
| CN105803239A (en) | Preparation method for micro-pore-diameter high-porosity nickel-chrome-molybdenum porous material | |
| CN104550906A (en) | Premixed bronze powder and preparation method and application thereof | |
| CN102162044B (en) | Preparation method of tungsten carbide/cobalt system porous material | |
| CN103397244A (en) | Preparation method of sintered Fe-Al-based porous alloy material with high-temperature oxidization resistance | |
| CN104195373B (en) | Powder sintered porous filter alloy, preparation method thereof and pre-compression molded body | |
| CN104630635A (en) | Iron-chromium-aluminum-based porous metal material and preparation method thereof | |
| CN103320638B (en) | The preparation method of sintered porous material | |
| CN103882325A (en) | Composite powder material for making high-performance abrasion resistant exhaust valve seat, and its application |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant |