JP5526940B2 - Method for producing porous aluminum sintered body - Google Patents

Description

  The present invention relates to a method for producing an aluminum porous sintered body suitable for a heat pipe having a foam metal on the inner surface of a pipe body.

In general, the structure of a heat pipe is, for example, a net or porous material called a wick is mounted in a sealed body made of copper or tungsten, and a small amount of hydraulic fluid such as water or sodium is enclosed. Yes. The wick is provided on the inner surface of the pipe body for circulating the hydraulic fluid by capillary action. The working fluid is a medium that easily changes between a gas phase and a liquid phase.

  Then, the hydraulic fluid sealed in the heat pipe absorbs heat from the outside and evaporates, and the evaporated hydraulic fluid is thermally transported to the heat radiating portion having a low temperature in the pipe. Release heat to the outside. The working fluid that has released the heat is condensed and liquefied again. At this time, the liquefied hydraulic fluid circulates inside the wick and moves to the heat receiving portion again by the capillary action of the wick. By repeating this cycle, the heat pipe transfers heat from the heat receiving portion to the heat radiating portion.

  Conventionally, an open pore type nickel-based or stainless-based foam metal is frequently used as the porous material in the wick. However, by using an aluminum-based foam metal as the porous material, it is possible to improve the thermal conductivity and reduce the weight of the heat pipe.

  Therefore, for example, in Patent Document 1 below, after adding a thickener to molten aluminum to increase the viscosity, titanium hydride as a foaming agent is added, and hydrogen gas generated by the thermal decomposition reaction of titanium hydride is added. There has been proposed a production method for obtaining a porous aluminum body by a foam melting method in which molten aluminum is solidified while being foamed.

  However, the porous metal plate used for the heat pipe is preferably obtained by the conventional foaming and melting method, whereas the pore diameter is preferably small as long as gas and fluid flow are ensured. Since foamed aluminum has large closed pores of several mm, there is a problem that it cannot be put into practical use.

By the way, when considering the contact surface of the electric or heat conducting member, it is difficult to physically make contact with the entire surface because there are usually some irregularities on the surface. For this reason, the electrical resistance or thermal resistance at the contact surface becomes extremely large compared to the physical property values of the material of each member itself. Therefore, for example, in order to reduce these resistances, a method of improving each member in contact with each other by using a bolt or the like and applying pressure to contact each other can be considered. In this case, the above-described resistance can be reduced by applying a pressure higher than the yield strength to the contact portion of each member and causing plastic deformation at the contact portion to increase the contact area.
However, since it is extremely difficult to apply a constant pressure to the entire contact surface, there is a problem that it is difficult to reduce electrical resistance and thermal resistance at the contact surface.

  Therefore, in order to solve this problem, for example, in Patent Document 2 below, a method has been proposed in which a metal porous plate (porous sheet) is sandwiched between contact surfaces to improve electrical connection.

  However, since the metal porous plate has a structure in which the metal skeleton forms pores as shown in FIG. 1 of the following Patent Document 2, the surface thereof is an end of the metal skeleton. Protrudes as it is and has irregular irregularities. Therefore, although electrical conduction can be obtained with a relatively low load, there is a problem that the number of contact points is small and a satisfactory low resistance value cannot be obtained.

  On the other hand, the inventors of the present invention, as Japanese Patent Application No. 2009-82498, mixed aluminum powder with a sintering aid powder containing titanium as a sintering aid element to obtain an aluminum mixed raw material powder. By adding a water-soluble resin binder and water to the mixed raw material powder, a slurry-like viscous composition containing pores is formed, and the viscous composition is formed into a pre-sintered body by a slurry method such as a doctor blade method. When the preform is heated to Tm (° C.) in a non-oxidizing atmosphere and the temperature at which the aluminum mixed raw material powder starts melting is Tm−10 (° C.) ≦ T ≦ 685 (° C.) The manufacturing method of the aluminum porous sintered compact which manufactures an aluminum porous sintered compact by heat-baking at the temperature T (degreeC) was proposed.

  According to the method for producing an aluminum porous sintered body, an aluminum porous sintered body having a three-dimensional skeleton shape in which extremely small pores having a pore diameter of 600 μm or less are formed and having an open pore type is easily obtained. There are advantages.

Japanese Patent Application Laid-Open No. 08-209265 Japanese Patent Laid-Open No. 53-061083

  However, in the method for producing a porous aluminum sintered body, since the viscous composition is dried and sintered by a slurry method such as a doctor blade method, foamed aluminum having a uniform porosity is easily obtained. Although obtained, there is a problem that it is not possible to obtain an aluminum porous sintered body having a contact surface for improving the degree of adhesion necessary for the wick adhered to the inner surface of the heat pipe and the peel strength against bending. there were.

  The present invention has been made in view of such circumstances, and has a high porosity having fine and sized open pores of 600 μm or less, and improves the heat exchange efficiency by improving the adhesion with the contact surface and bending. To provide a method for producing an aluminum porous sintered body that can easily and inexpensively obtain an aluminum porous sintered body having a plurality of three-dimensional net-like pores with improved peel strength against processing. It is to be an issue.

In order to solve the above-mentioned problems, the method for producing an aluminum porous sintered body according to claim 1 comprises mixing a sintering aid powder containing titanium and / or titanium hydride with aluminum powder to obtain an aluminum mixed raw material powder. Then, to this aluminum mixed raw material powder, a water-soluble resin binder, water, a plasticizer comprising at least one of polyhydric alcohol, ether and ester, and a water-insoluble hydrocarbon system having 5 to 8 carbon atoms By adding and mixing an organic solvent to form a viscous composition, the viscous composition is foamed and then dried to obtain a molded body having a plurality of three-dimensional network-like pores communicating with each other. While obtaining at least two or more types of the molded products having different pore diameters and / or porosity, at least two or more types having different pore diameters and / or porosity. When the temperature at which the aluminum mixed raw material powder starts to melt is Tm (° C.) in a non-oxidizing atmosphere and the temperature before the aluminum mixed raw material powder starts melting is Tm− By calcining at a calcining temperature T (° C.) satisfying 10 (° C.) ≦ T ≦ 685 (° C.), at least two types of aluminum porous sintered bodies having different pore diameters and / or porosity are obtained. An aluminum composite having an aluminum porous sintered body bonded together is obtained , the average particle diameter of the sintering aid powder is r (μm), and the blending ratio of the sintering aid powder is W mass. %, 1 ≦ μ ≦ 30 (μm), 1 ≦ W ≦ 20 (mass%), and 0.1 ≦ W / r ≦ 2. A method for producing an aluminum composite having a bonded body.

  The invention according to claim 2 is characterized in that, in the invention according to claim 1, the aluminum powder has an average particle diameter of 2 to 200 μm.

The invention according to claim 3 is the invention according to claim 1 or 2 , wherein the water-soluble resin binder is included within a range of 0.5% to 7% of the mass of the aluminum mixed raw material powder. It is characterized by being.

The invention according to claim 4 is the invention according to any one of claims 1 to 3 , wherein the aluminum mixed raw material powder is within a range of 0.02 to 3% of the mass of the aluminum mixed raw material powder. These surfactants are added.

According to the invention described in claims 1 to 4 , a sintering aid powder containing titanium as a sintering aid element is mixed with aluminum powder to obtain an aluminum mixed raw material powder, and a water-soluble resin bond to the aluminum mixed raw material powder A three-dimensional network that communicates with each other by adding and mixing a material, a plasticizer such as water, and a water-insoluble hydrocarbon-based organic solvent to form a viscous composition, which is foamed and then dried. The step of obtaining a molded body having a plurality of pores is obtained with at least two or more types of molded bodies having different pore diameters and / or porosity, and at least two or more types having different pore diameters and / or porosity. The formed body is laminated to form a pre-sintered formed body, and the temperature at which the aluminum mixed raw material powder starts melting in a non-oxidizing atmosphere is Tm (° C.). Sometimes, it has a three-dimensional skeleton structure in which small pores having a pore diameter of 600 μm or less are formed by heating and baking at a heating and baking temperature T (° C.) satisfying Tm-10 (° C.) ≦ T ≦ 685 (° C.), And the aluminum porous sintered compact by which the at least 2 or more types of molded object from which a pore diameter and / or a porosity differ was laminated | stacked can be obtained.

Here, the reason for limiting the heating and firing temperature to Tm-10 (° C) or higher is that the temperature at which the aluminum powder contained in the aluminum mixed raw material powder and the sintering aid powder containing titanium start the reaction is Tm-10 (° C). That's why. The temperature at which the aluminum mixed raw material powder starts melting is described as Tm because the pure aluminum melting point is 660 ° C., but industrially used aluminum contains iron and silicon as impurities, so the melting point is 660. It is because it becomes lower than ° C. On the other hand, the reason why the heating and firing temperature is limited to 685 ° C. or less is that when heated and held at a temperature higher than that temperature, a drop-shaped lump of aluminum is generated in the sintered body.

  At this time, as the aluminum powder, it is preferable to use a powder having a particle size such that the viscous composition is viscous enough to be molded into a desired shape. That is, when the average particle size is reduced, the mass of the water-soluble resin binder needs to be increased by increasing the mass of the water-soluble resin binder relative to the mass of the aluminum powder. When the pre-sintered shaped body is heated and fired, the amount of carbon remaining in the aluminum increases and the sintering reaction is hindered.

  On the other hand, when the particle diameter of the aluminum powder is too large, the strength of the porous sintered body is lowered. Therefore, as in the invention described in claim 2, preferably, the average particle diameter of the aluminum powder is set to 2 μm or more to prevent the inhibition of the sintering reaction by increasing the mass of the water-soluble resin binder, and to 200 μm or less. Ensuring the strength of the porous sintered body. More preferably, the average particle diameter of the aluminum powder is 7 μm to 40 μm.

Furthermore, in the present invention, the sintering aid powder has an average particle diameter r and a blending ratio W mass% of 1 (μm) ≦ r ≦ 30 (μm), 0.1 (mass%) ≦ W ≦ 20 (mass). %), and 0.1 ≦ W / r ≦ 2.
This is because when the mixing ratio W of the sintering aid powder exceeds 20% by mass, the sintering aid powder has contact points in the aluminum mixed raw material powder, and the reaction heat of aluminum and titanium cannot be controlled. At the same time, a desired porous sintered body cannot be obtained, so 0.1 (mass%) ≦ W ≦ 20 (mass%).

  Further, even within the range of 0.1 (mass%) ≦ W ≦ 20 (mass%), the reaction heat of aluminum and titanium may become too large depending on the particle size of the sintering aid powder, In some cases, the temperature of the aluminum melted by heat is further increased, the viscosity is lowered, and droplets are generated.

  Therefore, from the results of observing specimens prepared under various conditions with an electron microscope, the surface layer with a substantially constant thickness from the exposed surface side of the titanium particles within a range in which the calorific value can be controlled by the blending amount and particle size of titanium. It was found that only the part reacted with aluminum. Thus, it was experimentally derived that it is desirable that 1 (μm) ≦ r ≦ 30 (μm) and 0.1 ≦ W / r ≦ 2 in order to prevent the generation of droplets.

The meaning of 0.1 ≦ W / r ≦ 2 will be described below when titanium is used as the sintering aid powder. The average particle diameter of titanium is r, the number of titanium particles is N, and the titanium Assuming that the added mass is w, the specific gravity of titanium is D, and the amount of decrease in the titanium particle size due to the reaction with aluminum is d, the amount of heat of reaction Q is proportional to the volume of the reacted titanium, so Q∝4πr ² dN. Furthermore, since the addition amount of the titanium particles is calculated by the product of the average volume of one titanium particle and the number of titanium particles, w = 4 / 3πr ³ DN. Therefore, when the latter equation is substituted into the former equation, Q∝3wd / rD is obtained. Here, Q∝w / r from the observation result that 3 / D is a constant and d is substantially constant regardless of the sintering conditions. Therefore, by experimentally determining the range of W / r in which no droplets are generated and limiting it as described above, the generation of droplets due to excessive reaction heat between aluminum and titanium is prevented.

Further, when the water-soluble binder is contained in excess of 7% of the mass of the aluminum mixed raw material powder, the amount of carbon remaining in the pre-sintered molded body during heating and firing is increased, and the sintering reaction is caused. Be inhibited. On the other hand, if it is less than 0.5%, the handling strength of the green body before sintering cannot be ensured. For this reason, it is preferable that it is contained within the range of 0.5% to 7% of the mass of the aluminum mixed raw material powder as in the invention described in claim 3 .

In addition to this, by adding a surfactant to the aluminum mixed raw material powder as in the invention described in claim 4 , it is possible to effectively generate bubbles, and the amount of the surfactant added is mixed with aluminum. By making it 0.02% or more of the mass of the raw material powder, the effect due to the addition of the above-mentioned surfactant can be obtained, and by making it 3% or less, the amount of carbon remaining in the pre-sintered molded body increases. This can prevent the sintering reaction from being hindered.

It is the schematic of the shaping | molding apparatus used for the sintering pre-process of one Embodiment of the manufacturing method of the aluminum porous sintered compact of this invention. It is a partial cross section perspective view of the heat pipe using the aluminum porous sintered compact obtained with the manufacturing method of the aluminum porous sintered compact of this invention.

Hereinafter, an embodiment of a method for producing an aluminum porous sintered body according to the present invention will be described with reference to the drawings.
If the manufacturing method of this embodiment is demonstrated roughly, first, titanium and / or titanium hydride will be mixed with aluminum powder, and aluminum mixed raw material powder will be prepared (aluminum mixed raw material powder preparation process). And in this aluminum mixed raw material powder, a water-soluble resin binder, water, a plasticizer composed of at least one of polyhydric alcohol, ether and ester, and a water-insoluble hydrocarbon organic solvent having 5 to 8 carbon atoms, Are added and mixed to prepare the first viscous composition 3 and the second viscous composition 30 (viscous composition preparation step).

Next, as shown in FIG. 1, the slurry of the first viscous composition 3 is applied on the carrier sheet 8 to a predetermined thickness by the doctor blade method, and then the slurry of the second viscous composition 30 is further applied to the doctor. The pre-sintered molded body 15 is obtained by applying a predetermined thickness on the viscous composition 3 after coating by the blade method, foaming and then drying (pre-sintering step).
The pre-sintered compact 15 is heated and fired in a non-oxidizing atmosphere at Tm-10 (° C.) ≦ heating and firing temperature T ≦ 685 (° C.) (sintering step). Here, Tm (° C.) is a temperature at which the aluminum mixed raw material powder starts to melt.

Next, each process of the manufacturing method will be described in detail.
In the aluminum mixed raw material powder preparation step, aluminum powder having an average particle diameter of 2 to 200 μm is used. This is because when the average particle size is reduced, a large amount of water-soluble resin binder is added to the aluminum powder so that the viscous composition 3 is viscous enough to be molded into a desired shape, and before sintering. The molded body 15 needs to have handling strength. However, when a large amount of the water-soluble resin binder is added, when the pre-sintered molded body 15 is heated and fired, the amount of carbon remaining in the aluminum increases and the sintering reaction is hindered. On the other hand, when the particle diameter of the aluminum powder is too large, the strength of the finally obtained aluminum porous sintered body is lowered. Therefore, as the aluminum powder, those having an average particle diameter in the range of 2 to 200 μm, more preferably in the range of 7 to 40 μm are used as described above.

Further, a sintering aid powder containing titanium and / or titanium hydride is mixed with the aluminum powder. This is because, in the subsequent sintering step, the pre-sintered compact 15 is heated and fired at Tm-10 (° C.) ≦ heating and firing temperature T ≦ 685 (° C.), thereby generating a lump of droplets. This is because free sintering of aluminum is possible. Further, titanium hydride (TiH ₂ ) has a titanium content of 47.88 (molecular weight of titanium) / (47.88 + 1 (molecular weight of hydrogen) × 2) and is 95% by mass or more, and 470 to 530. Since it is dehydrogenated at 0 ° C. to become titanium, it is thermally decomposed to titanium by the above-mentioned heating and firing. Therefore, even when titanium hydride is mixed, free sintering of aluminum without forming a lump of droplets becomes possible.

  At that time, when the average particle diameter of titanium and / or titanium hydride is r (μm) and the blending ratio of titanium and / or titanium hydride is W (mass%), 1 (μm) ≦ r ≦ 30 ( μm), 0.1 (mass%) ≦ W ≦ 20 (mass%), and 0.1 ≦ W / r ≦ 2. That is, in the case of titanium hydride powder having an average particle diameter of 4 μm, the compounding ratio W is 0.4 ≦ 8% by mass because 0.1 ≦ W / 4 ≦ 2, and the titanium powder having an average particle diameter of 20 μm. In this case, the compounding ratio W is 2 to 40% by mass since 0.1 ≦ W / 20 ≦ 2, but from 0.1 (% by mass) ≦ W ≦ 20 (% by mass) to 2 to 20%. It becomes mass%.

  The average particle diameter of titanium hydride is 0.1 (μm) ≦ r ≦ 30 (μm), more preferably 4 (μm) ≦ r ≦ 20 (μm). If it is 1 μm or less, there is a risk of spontaneous ignition. On the other hand, if it exceeds 30 μm, the titanium hydride becomes titanium particles coated with a compound of aluminum and titanium after sintering. This is because the compound phase of aluminum and titanium is easily peeled off, and a desired strength can be obtained in the sintered body.

  Further, 0.1 (% by mass) ≦ W ≦ 20 (% by mass) is set when the mixing ratio W of the sintering auxiliary powder exceeds 20% by mass in the aluminum mixed raw material powder. This is because they have contact points, making it impossible to control the heat of reaction between aluminum and titanium, and making it impossible to obtain a desired porous sintered body.

  Further, even within the range of 0.1 (mass%) ≦ W ≦ 20 (mass%), depending on the particle size of the sintering aid powder, the reaction heat of aluminum and titanium may become too large, In some cases, the temperature of the aluminum melted by the heat of reaction further increases, the viscosity decreases, and droplets are generated.

  Therefore, from the results of observing specimens prepared under various conditions with an electron microscope, the surface layer with a substantially constant thickness from the exposed surface side of the titanium particles within a range in which the calorific value can be controlled by the blending amount and particle size of titanium. Only the part was found to be reacting with aluminum. Thus, it was experimentally derived that it is desirable that 1 (μm) ≦ r ≦ 30 (μm) and 0.1 ≦ W / r ≦ 2 in order to prevent the generation of droplets.

Regarding the meaning of 0.1 ≦ W / r ≦ 2, the case where titanium is used for the sintering aid powder will be described. The average particle diameter of titanium is r, the number of titanium particles is N, and the added mass of titanium is Assuming that w, the specific gravity of titanium is D, and the amount of decrease in the titanium particle size due to the reaction with aluminum is d, the amount of reaction heat Q is proportional to the volume of the reacted titanium, so that Q∝4πr ² dN. Furthermore, since the addition amount of the titanium particles is calculated by the product of the average volume of one titanium particle and the number of titanium particles, w = 4 / 3πr ³ DN. Therefore, when the latter equation is substituted into the former equation, Q∝3wd / rD is obtained. Here, Q∝w / r from the observation result that 3 / D is a constant and d is substantially constant regardless of the sintering conditions. Therefore, by experimentally determining the range of W / r in which no droplets are generated and limiting it as described above, the generation of droplets due to excessive reaction heat between aluminum and titanium is prevented.

  Next, in the viscous composition preparation step, the aluminum mixed raw material powder is made of at least one selected from the group consisting of polyvinyl alcohol, methylcellulose and ethylcellulose as a water-soluble resin binder, and polyethylene as a plasticizer. At least one selected from the group consisting of glycol, glycerin and di-N-butyl phthalate is added, respectively, and distilled water and alkylbetaine as a surfactant are added.

  Thus, when polyvinyl alcohol, methylcellulose, or ethylcellulose is used as the water-soluble resin binder, the amount added is relatively small. For this reason, the addition amount of the said water-soluble resin binder exists in the range of 0.5-7 mass% with respect to 100 mass parts of aluminum mixing raw material powder. If it exceeds 7% by mass with respect to 100% by mass of the aluminum mixed raw material powder, the amount of carbon remaining in the pre-sintered molded body 15 or the like during heating and firing is increased, and the sintering reaction is inhibited. This is because the handling strength of the pre-sintered molded body 15 is not ensured if it is less than mass%.

  Moreover, 0.02-3 mass% of alkylbetaines are added with respect to 100 mass parts of aluminum mixed raw material powder. If it exceeds 0.02% by mass with respect to 100% by mass of the aluminum mixed raw material powder, bubbles are effectively generated when the water-insoluble hydrocarbon-based organic solvent described later is mixed, and less than 3% by mass. This is because inhibition of the sintering reaction due to an increase in the amount of carbon remaining in the pre-sintered compact 15 or the like is prevented.

  And after kneading these, it is made to foam by mixing a C5-C8 water-insoluble hydrocarbon-type organic solvent, and the viscous composition 3 with which the bubble was mixed is adjusted. As this water-insoluble hydrocarbon organic solvent having 5 to 8 carbon atoms, at least one of pentane, hexane, heptane and octane can be used.

Next, in this embodiment, the pre-sintering process is performed using a molding apparatus as shown in FIG.
The molding apparatus 1 includes a first doctor blade 2, a hopper 4 of a first viscous composition 3, a second doctor blade 20, a hopper 40 of a second viscous composition 30, a preliminary drying chamber 5, a constant temperature / high humidity tank 6, Sintering in which an aluminum porous body before sintering is applied on the drying tank 7, the delivery reel 9 of the carrier sheet 8, the support rolls 10, 11, 12 of the carrier sheet 8 and the carrier sheet (coating material) 8. A roll 13 for guiding and supporting the pre-formed body 15, a peeling portion 23 for peeling the carrier sheet 8 from the pre-sintered molded body 15, a take-up reel 14 for the peeled carrier sheet 8, and a pre-sintered formed body 15 are predetermined. A cutter 16 that cuts into the size of is roughly configured.

  In the pre-sintering step, the first doctor blade 2 is applied to the upper surface (application surface) of the carrier sheet 8 where the first viscous composition 3 charged into the hopper 4 is continuously fed from the feed reel 9. After coating to a thickness of 0.05 to 5 mm, the second viscous composition 30 charged into the hopper 40 is applied to the upper surface of the first viscous composition 3 coated on the carrier sheet ( The coating surface is coated by the second doctor blade 20 to a thickness of 0.05 to 5 mm. Then, foaming is performed from the preliminary drying chamber 5 in the constant temperature / high humidity tank 6, and the bubbles are sized, and then dried in the drying tank 7 at a temperature of 70 ° C. Next, the pre-sintered molded body 15 sent out from the roll 13 is cut into a predetermined length by a cutter 16 or the like.

  The pre-sintered molded body 15 delivered through the foaming / drying process has a plurality of three-dimensional network mouth-shaped pores communicating with each other, and at least two types of moldings having different pore diameters and / or porosity. The body is laminated. In the laminated pre-sintered molded body 15, a dense layer forming molded body 15 a is disposed on the upper surface side of the carrier sheet 8, and a porous layer forming molded body 15 b is disposed on the upper surface side of the dense layer forming molded body 15 a. Be placed. In addition, the first viscous composition 3 and the second viscous composition 30 have bubbles formed by vaporization of the foaming agent contained therein, and the composition containing the metal powder aggregates around the bubbles, so that A part to be a skeleton is formed. The bubbles are distributed three-dimensionally and are arranged in contact with each other. Since the bubbles try to swell in a spherical shape, the skeleton has a three-dimensional network-like structure with substantially spherical continuous pores.

  Further, since the foaming agent tends to swell in a spherical shape on the lower surface of the first viscous composition 3 on the carrier sheet 8 side in the pre-sintered compact 15, a plurality of substantially circular shapes communicating with each bubble are provided. A hole is formed. Here, the portion where the bubbles are not in contact forms a flat planar portion along the surface of the carrier sheet 8, and the portion of the bubbles becomes a hole. And since one section of the bubble appears as the hole on the surface, the diameter of the hole is smaller than the hole communicating with the bubble. Moreover, the area of the said planar part can be adjusted by adjusting the wettability of the carrier sheet 8 and the viscous composition 3.

  On the other hand, the upper surface, which is the surface opposite to the carrier sheet 8, of the second viscous composition 30 in the pre-sintered molded body 15 is formed so as to protrude from the surface of the viscous composition 30 to which bubbles are applied. However, since the viscous composition 30 containing the metal powder aggregates on the surface without protruding from the surface due to surface tension, a planar portion spreading in a planar shape is formed around the protruding bubbles. become. In addition, the protruding bubble portion becomes a hole communicating with the hole when the bubble is removed by drying. Also in this case, the diameter of the hole is smaller than the diameter of the hole for the same reason as described above. Further, for example, by changing the preheating temperature after coating with the second doctor blade 20, the surface viscosity and surface tension of the viscous composition 30 can be changed to adjust the area of the planar portion.

  Therefore, next, in the sintering step, the pre-sintered compact 15 is placed on an alumina setter with zirconia powder spread, and 1 at 520 ° C. in an argon atmosphere having a dew point of −20 ° C. or less. Temporary firing is performed by heating for a period of time. As a result, debinding that volatilizes and / or decomposes the binder solution of the water-soluble resin binder component, the plasticizer component, distilled water, and alkylbetaine of the green compact 15 before sintering is performed, and hydrogen is used as the sintering aid powder. When titanium fluoride is used, dehydrogenation is performed.

Then, the pre-sintered compact 1514 after temporary firing is heated and fired at Tm−10 (° C.) ≦ heating and firing temperature T ≦ 685 (° C.) to obtain an aluminum porous sintered body.
The heating and baking are performed in the above range T because the pre-sintered compact 15 is heated to the melting temperature Tm (° C., but the reaction between aluminum and titanium is considered to start. Since the eutectic alloy elements such as Fe and Si are contained in a very small amount as impurities and the melting point is lowered, it is considered that the reaction between aluminum and titanium is started by heating to Tm-10 (° C.). In practice, while the melting point of aluminum is 660 ° C., with atomized powder having a purity of about 98% to 99.7% distributed as pure aluminum powder, around 650 ° C. is the melting start temperature. Become.

  On the other hand, the peritectic temperature of aluminum and titanium is 665 ° C., and further, when the latent heat of fusion is input, the sintered body of aluminum melts, so it is necessary to maintain the furnace atmosphere temperature at 685 ° C. or lower. .

  In addition, in order to suppress the growth of the oxide film of the aluminum particle surface and the titanium particle surface, it is necessary to perform the heat baking in the sintering process in a non-oxidizing atmosphere. However, if the preheating is held at a heating temperature of 400 ° C. or lower for about 30 minutes, the oxide film on the surface of the aluminum particles and the surface of the titanium particles does not grow so much even when heated in air. The molded body 15 may be once heated and held in air at 300 ° C. to 400 ° C. for about 10 minutes to remove the binder, and then heated and fired at a predetermined temperature in an argon atmosphere.

  The aluminum porous sintered body 17 thus obtained has a metal skeleton having a three-dimensional network structure made of a porous metal sintered body and has a pore diameter and / or porosity as shown in FIG. Two or more kinds of porous bodies having different values are laminated. The laminated porous body includes a dense layer 17a having a pore diameter of 0.1 to 20 μm and a porosity of 5 to 50%, and a porous layer 15b having a pore diameter of 20 to 600 μm and a porosity of 70 to 97%. It is configured. Further, the Al—Ti compound is dispersed substantially uniformly in the porous metal sintered body, and 20 or more pores are formed per 1 cm of the linear length, and the dense layer 17a is 5 to 50% and the porous layer 17b. Has an overall porosity of 70-97%.

  Furthermore, when the aluminum porous sintered body 17 obtained by the method for producing an aluminum porous sintered body of the present embodiment is used for a heat pipe 18 as shown in FIG. Each flat plate is folded into a U-shape. Next, the aluminum porous sintered body 17 is bonded to each bent aluminum plate. At this time, the dense porous layer 17a side of the aluminum porous sintered body 17 is disposed in close contact with the inner surface of the aluminum plate bent in a U-shape.

  Then, the aluminum porous sintered body 17 side bonded to each of the bent aluminum plates is faced to each other, and each long side portion is caulked to form a prismatic pipe, and in the prismatic pipe After filling water as the working fluid 20 and depressurizing the inside, a sealed heat pipe can be manufactured by closing both sides of the open corps with an aluminum plate.

  As shown in FIG. 2, the heat pipe 18 absorbs external heat from the heat receiving portion 21 at one end of the pipe, and the internal working fluid 20 evaporates. At this time, since the dense layer 17a of the aluminum porous sintered body 17 adhered to the inner surface of the pipe is in close contact with the flat planar portion 17c, heat from the outside can be efficiently absorbed. Then, the evaporated working fluid 20 becomes steam and is transported by heat to the heat radiating portion 22 having a low temperature in the pipe. In this heat radiating portion 22, heat is released from the transported steam to the outside. Also at this time, the dense layer 17a of the porous aluminum sintered body 17 adhered to the inner surface of the pipe is in close contact with the flat planar portion 17c, so that heat can be efficiently released to the outside. Furthermore, the working fluid 20 that has released the heat is condensed and liquefied again. The liquefied hydraulic fluid 20 is absorbed by the capillary action of the porous layer 17b of the aluminum porous sintered body 17 serving as the wick 19, and moves to the heat receiving portion again by circulating. Then, the hydraulic fluid 20 that has moved to the heat receiving portion 21 again absorbs external heat and evaporates. By repeating this cycle, the heat pipe 18 transfers heat from the heat receiving portion 21 to the heat radiating portion 22.

  Therefore, by using the porous aluminum sintered body 17 obtained by the manufacturing method of the present invention for the wick 19 of the heat pipe 18, the heat exchange efficiency between the heat absorption by the heat receiving portion 21 and the heat release by the heat radiating portion 22 is achieved. In addition, since a very small hole having a hole diameter of 600 μm or less is formed in the three-dimensional skeleton shape, the gas inside the minute hole becomes a boiling nucleus, and volatilization in the discharge part 22 of the working fluid 20 occurs. Is performed smoothly and the cooling rate can be increased.

  In addition, since the dense layer 17a of the aluminum porous sintered body 17 is in close contact with the aluminum plate by the flat planar portion 17c, the aluminum porous sintered body can be formed even if the shape of the heat pipe 18 is deformed by bending. The bonded body 17 is not peeled off from the aluminum plate.

  The method for producing a porous aluminum sintered body of the present invention can be used when producing a wick of a heat pipe.

DESCRIPTION OF SYMBOLS 1 Molding apparatus 2 1st doctor blade 20 2nd doctor blade 3 1st viscous composition 30 2nd viscous composition 4, 40 Hopper 5 Predrying chamber 6 High humidity tank 7 Drying tank 8 Carrier sheet 9 Delivery reel 10, 11, 12 Support Roll 13 Guide / Support Roll 14 Take-up Reel 15 Pre-Sintered Molded Body 15a Dense Layer Forming Body 15b Porous Layer Forming Form 16 Cutter 17 Aluminum Porous Sintered Body 17a Dense Layer 17b Porous Layer 17c Planar Part 18 Heat pipe
19 Wick 20 Hydraulic fluid 21 Heat receiving part 22 Release part

Claims (4)

The aluminum powder is mixed with a sintering aid powder containing titanium and / or titanium hydride to obtain an aluminum mixed raw material powder, and then the aluminum mixed raw material powder is mixed with a water-soluble resin binder, water, polyhydric alcohol, ether. And a plasticizer comprising at least one of esters and a water-insoluble hydrocarbon-based organic solvent having 5 to 8 carbon atoms are added and mixed to form a viscous composition, and the viscous composition is foamed and then dried. Thus, by obtaining a molded body having a plurality of three-dimensional network-shaped pores communicating with each other, at least two or more types of the molded bodies having different pore diameters and / or porosity are obtained. / Or laminated at least two types of molded bodies having different porosity to form a molded body before sintering,
Tm-10 (° C.) ≦ T ≦ 685 (° C.), where Tm (° C.) is the temperature at which the aluminum mixed raw material powder starts melting in a non-oxidizing atmosphere. By heat-firing at a heat-firing temperature T (° C.), an aluminum porous sintered body in which at least two types of aluminum porous sintered bodies having different pore diameters and / or porosity are integrally bonded is provided. An aluminum composite ,
When the average particle diameter of the sintering aid powder is r (μm) and the blending ratio of the sintering aid powder is W mass%, 1 (μm) ≦ r ≦ 30 (μm), 1 ≦ W ≦ 20 (mass%) and 0.1 ≦ W / r ≦ 2. A method for producing an aluminum composite having an aluminum porous sintered body,   2. The method for producing an aluminum composite having an aluminum porous sintered body according to claim 1, wherein the aluminum powder has an average particle diameter of 2 to 200 μm. 3. The porous aluminum sintered body according to claim 1, wherein the water-soluble resin binder is contained within a range of 0.5% to 7% of a mass of the aluminum mixed raw material powder. The manufacturing method of the aluminum composite which has this. The surfactant within the range of 0.02 to 3% of the mass of the aluminum mixed raw material powder is added to the aluminum mixed raw material powder . A method for producing an aluminum composite having an aluminum porous sintered body.

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