JP5614906B2 - Method for producing metal matrix composite - Google Patents

Description

  The present invention generally relates to a metal matrix composite having neutron absorption performance, and more particularly, properties such as plastic workability, thermal conductivity, room temperature or high temperature strength, high rigidity, wear resistance, low thermal expansion, etc. The present invention relates to a method for producing an excellent metal matrix composite.

Until now, as a procedure to produce composite materials with aluminum as the parent phase by powder metallurgy,
(1) Mixing ceramic particles such as Al ₂ O ₃ , SiC, B ₄ C, BN, aluminum nitride, and silicon nitride, which are reinforcing materials, with aluminum powder that is a parent phase,
(2) Thereafter, the mixed powder can be encapsulated or cold compression molded,
(3) Thereafter, degassing and sintering are performed.
(4) Mold into the desired shape,
Things were known.

  As the sintering method of (3), (A) a method of simply heating, (B) a method of heating while applying pressure such as hot press, (C) hot extrusion, hot forging, hot rolling, etc. There are a method of pressure sintering by hot plastic working, (D) a method of applying current and sintering while applying pressure (for example, Patent Document 1), a method of (E) combining these methods, and the like. In some cases, degassing also serves as sintering.

  In recent years, applications have been developed as aluminum composites that require not only strength but also high Young's modulus, wear resistance, low thermal expansion, and neutron absorption performance. In general, it is possible to increase the neutron absorption function by increasing the addition amount of ceramics having a neutron absorption function. However, by simply increasing the addition amount, sinterability, extrudability, rollability and Plastic workability, such as forgeability, will fall remarkably.

  From this point of view, a method is also considered in which ceramics are preformed and molten aluminum alloy is infiltrated therein to uniformly disperse high-concentration ceramics in the matrix. However, in reality, there is a possibility that defects such as insufficient penetration of the molten metal and sink marks during solidification may occur.

  Patent Document 2 was invented as a solution to the above-described problems, and (a) a step of preparing a mixed material by mixing aluminum powder and ceramic particles; and (b) the mixed material together with a metal plate. A step of forming a clad material in which the sintered body is coated with a metal plate material by applying current and pressure sintering; and (c) a step of plastically processing the clad material to obtain an aluminum composite material. The manufacturing method of the aluminum composite material characterized by these is disclosed.

  In Patent Document 2, prior to rolling a mixed material prepared by mixing aluminum powder and ceramic particles, the mixed material is sandwiched between metal plates and subjected to current and pressure sintering to maintain a predetermined shape. The clad material had to be preformed. This is because, unless the clad material is preformed in such a shape-preserved form, it is difficult and practically impossible to roll the clad material.

  As described above, in Patent Document 2, the clad material is preliminarily molded in a form in which the shape is maintained, specifically, the current pressure sintering operation is indispensable. Cost reduction has not been achieved. In this way, there is a keen desire to solve these problems.

On the other hand, Patent Document 3 discloses a structural feature of a neutron absorbing material constituting an intermediate portion of a clad material, although it is not a clad material as in the present invention. In this patent document 3, the neutron absorber is manufactured by mixing aluminum powder powder and B ₄ C particles as ceramic particles, sintering the mixture, and extruding the sintered body.

As described above, in Patent Document 3, since the mixed material is adjusted by simply mixing the aluminum powder and the B ₄ C particles, the density of the mixed material preformed by sintering is the same as that of the aluminum powder and B _4. It was only obtained by simply mixing with C particles, and the density was “sparse”, specifically, the bulk density was only about 90%. Thus, even if the mixed material of sparse density is preformed by the sintering operation and then subjected to the rolling operation, the density of the intermediate layer composed of the aluminum powder and B ₄ C particles of the resulting rolled body is as follows. However, it has been pointed out that the mechanical properties such as the tensile strength, the bending strength, and the thermal conductivity are poor at only 95% at most.

JP 2001-329302 A International Publication No. WO2006 / 070879 U.S. Pat.No. 5,965,829

The present invention has been made in view of the above circumstances, and is a metal-based composite material that can improve the mechanical characteristics while ensuring the B ₄ C content sufficiently from the viewpoint of the neutron absorption function. The main purpose is to provide a manufacturing method.

  Another object of the present invention is to provide a method for producing a high-quality metal matrix composite that can achieve neutron absorption characteristics and tensile strength at the same time or higher than the specifications required by the market.

  Another object of the present invention is to provide a method for producing a metal matrix composite that can achieve neutron absorption characteristics and 0.2% proof stress at the same time or higher than the specifications required by the market.

  Still another object of the present invention is to provide a method for producing a metal matrix composite that can achieve neutron absorption characteristics and thermal conductivity at the same time or higher than the specifications required by the market.

  In the present specification and claims, aluminum means pure aluminum and an aluminum alloy.

In particular, the method for producing a metal matrix composite according to an embodiment of the present invention includes filling a hollow flat metal case with a mixture of metal powder and ceramic particles having neutron absorption characteristics. Tapping is carried out to increase the packing density, and this is hermetically sealed to constitute a rolled body, the rolled body is preheated, and the preheated rolled body is rolled. That is, the metal matrix composite manufacturing method of the present invention includes (a) a step of preparing the mixed material by mixing the metal powder and the ceramic particles, and (b) sealing the lower case and the lower case. A metal case having an upper case formed on the lower case; and (c) the mixed material in a state in which a sleeve main body closely contacting the upper edge of the lower case is superposed on the lower case. After the tapping, the sleeve body is lifted upward, and then the scraper is moved along the upper edge of the lower case so as to be flush with the upper edge of the lower case. A filling step , (d) a step of preparing a rolled body from the metal case filled with the mixed material by covering the lower case with the upper case and sealing, and (e) the covering Pressure The body, the steps of the mixing material is preheated to maintain the powder state, and cold rolled the rolled body preheated in (f) said preheating step has a step of obtaining a metal composite material.

Thus, in this embodiment, the material to be rolled is sealed by filling the metal case with the mixed material and then sealing the metal case in a state where the packing density of the mixed material is increased by tapping. Will be composed. And this to-be-rolled body is the state by which the mixed material as a powder was pinched | interposed from the upper and lower sides by the metal plate which each defines the upper and lower surfaces of metal cases. Consequently, by cold rolling after having preheated the rolled material, during the layer and the metal powder and ceramic particles are mixed in a state of being kept high packing density, up and down it with a metal Thus, the clad material sandwiched between the two is surely formed.

  Further, in the present invention, in the rolled body constituting the material to be rolled, the upper surface of the mixed material corresponding to the intermediate layer of the metal matrix composite having the cladding structure, and the upper plate of the upper case corresponding to the upper layer in the cladding structure Are in close contact with each other, and the lower surface of the mixed material corresponding to the intermediate layer of the cladding structure and the lower plate of the lower case corresponding to the lower layer in the cladding structure are in close contact with each other.

  In the metal matrix composite obtained by rolling such a material to be rolled, the layers adjacent to each other are firmly joined together. As a result, the mechanical strength of the metal matrix composite is greatly increased. Will increase. Moreover, in this invention, since there is no ceramic particle | grains which become a starting point of a fracture | rupture or wear a die | dye etc. on the metal matrix composite surface, a favorable rolled material can be obtained. In addition, the upper and lower surfaces of the hollow case will function as the upper and lower metal plates when forming the cladding, so the configuration as the cladding material will be completed with the mixed material filled in the case. The process is simplified. Furthermore, since the mixed material in the hollow case is used in the rolling process in the form of powder, the bulk density maintained in the state where the mixed material is filled in the case is up to about 65%. Is done.

  In a further embodiment of the present invention, the aluminum powder is a pure Al powder having a purity of 99.0% or more or an alloy powder containing 0.2 to 2% by weight of any one of Mg, Si, Mn, and Cr in Al. The ceramic particles occupy 0.5 to 60% by mass when the total mass of the mixed material is 100% by mass.

In general, ceramic particles added as a material having neutron absorption characteristics, such as B ₄ C, have a very high hardness compared to metals. For this reason, when a metal powder containing a large amount of ceramic particles is sintered to form a sintered body and the sintered body is plastically processed as in the past, the ceramic particles on the surface become the starting point of fracture, and plasticity There is a strong tendency to crack in the processed material. There is also a problem that the extrusion die, the rolling roller, the forging die and the like are worn.

  However, in the present invention, since the metal matrix composite is manufactured by omitting the electric pressure sintering process, there is no ceramic particle on the surface that becomes a starting point of fracture or wears a die or the like. As described above, the first feature of the present invention is that the effect of obtaining a good rolled material can be exhibited uniquely.

  Further, when clad by sandwiching the mixed material between the upper and lower sides with the metal plate material, the upper and lower surfaces of the hollow case function as the upper and lower metal plate materials when forming the clad. As a result, the configuration as the clad material is completed in a state where the mixed material is filled in the case. This also simplifies the manufacturing process.

  In this case, the purpose of increasing the powder density was to make it possible to maintain the shape sufficient for the mixed material to be subjected to the rolling process, so that, for example, the bulk density of the powder is 98%. In contrast, in the present invention, the mixed material is used in the rolling process in the form of powder, so that the mixed material is filled in the case. In this state, the bulk density to be maintained is up to about 65%.

  These and other objects, features, and advantages of the present invention will become apparent from the following detailed description when read in conjunction with the accompanying drawings.

It is a perspective view which shows the structure of the case used in the method of the 1st Example of this invention. It is a figure which shows the structure of the reinforcement frame used in the method of the 1st Example of this invention. It is a longitudinal cross-sectional view which shows the case of the state with which mixed powder was filled. It is a longitudinal cross-sectional view of the lower case in the Example of this invention. It is a longitudinal cross-sectional view of a state in which a sleeve is superimposed on the lower case in the embodiment. It is a longitudinal cross-sectional view of the state which injected the mixed material into the space where the lower case and the sleeve in the said Example were overlapped. It is a longitudinal cross-sectional view of the state which injected the mixed material into the space where the lower case and the sleeve in the said Example were overlapped, and implemented the tapping. In the above embodiment, the mixture is put into the space where the lower case and the sleeve are overlapped and tapping is performed. Then, the sleeve is removed, the scraper is moved along the upper edge of the lower case, and the mixture protrudes above the lower case. It is a longitudinal cross-sectional view of the state which is going to scrape off the part of material. It is the longitudinal cross-sectional view of the state which the part of the mixed material which protruded above the lower case in the said Example was scraped off and was collect | recovered in the collection box. It is a longitudinal cross-sectional view of a state in which the upper case is to be fitted from above after the mixed material is filled in the lower case in the embodiment so that the upper surface thereof is flush with the upper edge of the lower case. It is a longitudinal cross-sectional view of the to-be-rolled body of the state with which the mixed material was fully filled in the space where the lower case and the upper case in the said Example were overlapped. Is a graph showing the correlation between the ^{10 B} area density and neutron transmittance in this embodiment. It is the photograph (magnification 750 times) which carried out the SEM imaging | photography of the surface state of the mixed material before tapping in the visual field 1. It is the photograph (magnification of 750 times) which carried out SEM imaging | photography of the surface state of the mixed material before tapping in the visual field 2 (position different from the said visual field 1). It is the photograph (magnification of 750 times) which carried out the SEM imaging | photography of the surface state of the mixed material before tapping in the visual field 3 (position different from the said visual field 1 and the said visual field 2). It is the photograph (magnification 750 times) which carried out the SEM image of the surface state of the mixed material after tapping in the visual field 4. It is the photograph (magnification of 750 times) which carried out SEM imaging | photography of the surface state of the mixed material after tapping in the visual field 5 (position different from the said visual field 4). It is the photograph (magnification of 750 times) which carried out the SEM imaging | photography of the surface state of the mixed material after tapping in the visual field 6 (position different from the said visual field 4 and the said visual field 5). It is a microscope picture (enlarged 100 times) near the skin layer of the clad material as the final product obtained by carrying out the method of the present invention. It is a microscope picture (enlarged 400 times) of the vicinity of the skin layer of the clad material as the final product obtained by carrying out the method of the present invention. FIG. 8 is a photomicrograph (enlarged 100 times) in the vicinity of the intermediate layer of the clad material shown in FIG. 7. 10 is a photomicrograph (enlarged by 400 times) in the vicinity of the intermediate layer shown in FIG. 9. It is a diagram which shows the correlation between ¹⁰ B area density of a neutron absorber, tensile strength, and a neutron absorption factor.

  According to the first aspect, the metal matrix composite of the present invention has a pair of metal plates with a mixed material sandwiched therebetween, and the mixed material comprises metal powder and ceramic particles having a neutron absorbing function. In the metal matrix composite, the theoretical density ratio of the intermediate layer composed of the mixed material is 98% or more, and the percentage of the total thickness of both metal plates is 15% or more. It is characterized by being within a range of 25% or less.

  According to the second aspect, the metal matrix composite of the present invention is formed in close contact with an intermediate layer comprising metal powder and ceramic particles having a neutron absorption function, and one surface of the intermediate layer. A metal matrix composite material made of a metal matrix composite material comprising a metal first skin layer and a metal second skin layer formed in close contact with the other surface of the intermediate layer, The theoretical density ratio of the intermediate layer is 98% or more, and the percentage of the total thickness of the total thickness of the first and second skin layers is in the range of 15% or more and 25% or less. It is characterized by that.

  Hereinafter, after explaining the raw materials to be used, the manufacturing method of the metal matrix composite according to the present invention will be described, and finally the metal matrix composite according to the embodiment of the present invention will be described in detail.

(1) Description of raw materials Base material aluminum powder In the preferred embodiment, the aluminum powder used as the base material of the main body is an Al-based alloy, specifically, A 1100 according to JIS standards (AA 1100 according to AA standards). It is formed from the aluminum alloy prescribed | regulated by. Specifically, silicon Si: 0.25 wt% or less, iron Fe: 0.40 wt% or less, copper Cu: 0.05 wt% or less, manganese Mn: 0.05 wt% or less, magnesium Mg: 0.05 Wt% or less, chromium Cr: 0.05 wt% or less, zinc Zn: 0.05 wt% or less, vanadium V: 0.05 wt% or less, titanium Ti: 0.03% wt% or less, the balance being aluminum and inevitable impurities It is formed from the material which has the composition component which makes it.

  However, in the present invention, the composition of the aluminum powder is not particularly limited. For example, as aluminum powder, pure aluminum (JIS 1050, 1070, etc.), Al—Cu alloy (JIS 2017, etc.), Al—Mg—Si alloy (JIS 6061, etc.), Al—Zn—Mg alloy (JIS 7075) are used. Etc.), powders of various types of alloys such as Al—Mn alloys can be used alone or in admixture of two or more.

  In short, the composition of the aluminum alloy powder to be selected is determined in consideration of desired characteristics, deformation resistance at the time of subsequent molding, the amount of ceramic particles to be mixed, raw material costs, and the like. For example, pure aluminum powder is preferable when it is desired to improve the workability and heat dissipation of the aluminum composite material. Pure aluminum powder is also advantageous in terms of raw material costs compared to the case of aluminum alloy powder. In addition, it is preferable to use a pure aluminum powder having a purity of 99.5% by mass or more (usually a commercially available pure aluminum powder is 99.7% by mass or more).

  In addition, when imparting neutron absorption ability, in other words, when it is desired to keep neutron permeability low, boron compounds are used as ceramic particles described later. Here, when it is desired to further increase the obtained neutron absorption capability, at least one element having neutron absorption capability such as hafnium (Hf), samarium (Sm), gadolinium (Gd) is preferably used in the aluminum powder. 0.1-50 mass% can be added to.

  When high temperature strength is required, titanium (Ti), vanadium (V), chromium (Cr), manganese (Mn), magnesium (Mg), iron (Fe), copper (Co), nickel (Ni ), Molybdenum (Mo), niobium (Nb), zirconium (Zr), strontium (Sr) and the like can be added to the aluminum powder. When room temperature strength is required, at least one of silicon (Si), iron (Fe), copper (Cu), magnesium (Mg), zinc (Zn), and the like can be added to the aluminum powder. . In any case, each element can be added at a ratio of 7% by weight or less, and in the case of mixing two or more elements at a ratio of 15% by weight or less in total.

  Although the average particle diameter of the aluminum powder is not particularly limited, a powder having an upper limit of generally 200 μm or less, preferably 100 μm or less, more preferably 30 μm or less can be used. The lower limit of the average particle diameter is not particularly limited as long as it can be produced, but is usually 0.5 μm or more, preferably 10 μm or more. In particular, the particle size distribution of the aluminum powder can be 100 μm or less, and the average particle size of ceramic particles as a reinforcing material to be described later can be 40 μm or less. In this case, the reinforcing material particles are uniformly dispersed, and there are very few dilute portions of the reinforcing material particles, which is effective in stabilizing the characteristics of the metal matrix composite.

  Since the average particle size of the aluminum alloy powder is likely to crack during rolling when the difference from the average particle size of ceramic particles described later is large, it is preferable to reduce the difference in average particle size. If the average particle size becomes too large, uniform mixing with ceramic particles that cannot increase the average particle size becomes difficult. On the other hand, if the average particle size is too small, aggregation is likely to occur between the fine aluminum alloy powders, and uniform mixing with the ceramic particles becomes very difficult. Further, by setting the average particle size of the aluminum particles to an average particle size within such a suitable range, it is possible to obtain further excellent processability, formability, and mechanical properties.

  The average particle diameter of the aluminum powder in the present invention is a value determined by a laser diffraction particle size distribution measurement method. The powder shape is not limited. For example, the aluminum powder may have any shape such as a teardrop shape, a true spherical shape, a spheroid shape, a flake shape, or an indefinite shape.

  The manufacturing method of the said aluminum powder is not limited at all. For example, the aluminum powder can be produced according to a known method for producing metal powder. Examples of the production method include an atomizing method, a melt spinning method, a rotating disk method, a rotating electrode method, and other rapid solidification methods. Here, from the viewpoint of industrial production, the atomizing method is preferable, and in particular, the gas atomizing method of manufacturing powder by atomizing a molten metal is preferable.

  In the atomizing method, it is preferable to atomize the molten metal by heating it to 700 to 1200 ° C. This is because more effective atomization can be performed by setting the temperature range. Further, the atomizing medium / atmosphere during atomization may be air, nitrogen, argon, helium, carbon dioxide, water, or a mixed gas thereof, but the atomizing medium is air, nitrogen gas or argon from an economic viewpoint. It is preferable to use gas.

Ceramic particles As ceramics mixed with aluminum powder and used to form the main body, there are Al ₂ O ₃ , SiC, B ₄ C, BN, aluminum nitride, silicon nitride, and the like. These ceramics are used in powder form, and these can be used alone or as a mixture, and are selected depending on the use of the composite material. Here, boron (B) has the ability to absorb neutrons (that is, the ability to inhibit neutron transmission). Therefore, when boron-based ceramic particles are used, the aluminum composite material can also be used as a neutron absorber. In that case, examples of boron-based ceramics include B ₄ C, TiB ₂ , B ₂ O ₃ , FeB, and FeB ₂ . These boron-based ceramics are used in the form of powder, and these can be used alone or as a mixture. In particular, it is preferable to use boron carbide B ₄ C containing a large amount of ¹⁰ B, which is an isotope of B that absorbs neutrons well.

  The ceramic particles are preferably contained in the above-described aluminum alloy powder in an amount of 0.5% by mass to 90% by mass. More preferably, it is 5 mass%-60 mass%, More preferably, it is 5 mass%-45 mass%. The reason for setting it as 0.5 mass% or more is that when it is less than 0.5 mass%, the composite material cannot be sufficiently strengthened. The reason why it is 90% by mass or less is that when it is more than 90% by mass, sintering is difficult, deformation resistance at the time of plastic processing is high, plastic processing is difficult, and the molded body becomes brittle and easily breaks. This is because there is a problem. In addition, the bondability between the aluminum particles and the ceramic particles also deteriorates, voids are easily formed, the desired functions cannot be obtained, and the strength and thermal conductivity are reduced. Furthermore, the machinability as an aluminum-based composite material also decreases.

The average particle diameter of ceramic particles such as B ₄ C and Al ₂ O ₃ is arbitrary, but 1 to 30 μm is preferable. As described in relation to the average particle size of the aluminum powder, the particle size difference between these two types of powders is appropriately selected according to the required specifications. For example, the average particle size of the ceramic particles is more preferably 5 μm or more and 20 μm or less. Here, if the average particle size of the ceramic particles is larger than 20 μm, there is a problem that the saw blades are worn immediately during cutting. If the average particle size of the ceramic particles is smaller than 5 μm, these fine powders tend to aggregate with each other, and uniform mixing with the aluminum powder may be very difficult.

  The average particle diameter of the ceramic particles of the present invention is a value determined by a laser diffraction particle size distribution measurement method. The powder shape of the ceramic particles is not limited, and may be any one of a teardrop shape, a true shape, a spheroid shape, a flake shape, an indefinite shape, and the like.

Case As the metal case, upper case and lower case, case main body and plug member used in the manufacturing method according to the present invention, any metal can be used as long as it has excellent adhesion to the mixed material and is suitable for rolling. Preferably, it is made of aluminum or stainless steel. For example, in the case of an aluminum case, pure aluminum (JIS 1050, 1070, etc.) is preferably used. On the other hand, as a case material, an Al—Cu alloy (JIS2017 etc.), an Al—Mg alloy (JIS5052 etc.), an Al—Mg—Si alloy (JIS6061 etc.), an Al—Zn—Mg alloy (JIS7075 etc.), Various types of alloy materials such as Al-Mn alloys can also be used.

  The composition of aluminum to be selected is determined in consideration of desired characteristics, cost, and the like. For example, pure aluminum is preferred when it is desired to improve workability and heat dissipation. Pure aluminum is also advantageous in terms of raw material costs compared to aluminum alloys. Further, when it is desired to further increase the strength and workability, an Al—Mg alloy (JIS 5052 or the like) is preferable. Furthermore, when it is desired to further increase the neutron absorption ability, at least one element having neutron absorption ability such as Hf, Sm, Gd, etc., can be added, preferably 1 to 50% by mass.

(2) Description of Manufacturing Process 2-1: Mixing Material Adjustment Process Aluminum powder and ceramic particles are prepared, and these powders are mixed uniformly. One kind of aluminum powder may be used, or a plurality of kinds may be mixed. Only one kind of ceramic particles may be used, or a plurality of kinds, for example, B ₄ C and Al ₂ O ₃ may be mixed. The mixing method of the aluminum powder and the ceramic particles may be a known method. For example, various mixers such as a V blender and a cross rotary mixer, a vibration mill, a planetary mill and the like are used, and a predetermined time (for example, 10 minutes to 10 hours). About) What should be mixed. Further, the mixing may be either dry or wet. Moreover, you may add suitably grinding media, such as an alumina and a SUS ball | bowl, for the purpose of crushing in the case of mixing.

  Basically, in this mixed material adjusting step, aluminum powder and ceramic particles are mixed to prepare a mixed material, and this powder mixed material is directly sent to the next step.

2-2: Case Preparation Step In this case preparation step, a hollow flat metal case filled with the mixed material manufactured in the above-described mixed material adjusting step is prepared.

  Specifically, the lower case 12 and the upper case 14 are prepared for configuring the metal case 10. The lower case 12 is made of aluminum, and is formed in a shape including side plates 12A, 12B, a front plate 12C, a rear plate 12D facing each other as shown in FIG. 1, and a bottom plate 12E as shown in FIG. 2B. . The upper case 14 is made of aluminum and is made of the same material as that of the lower case 12, and as shown in FIG. 1, the side plates 14A and 14B, the front plate 14C, the rear plate 14D, which face each other, and FIG. As shown in FIG. 4, the upper plate 14E is formed into a shape having the shape. More specifically, the lower case 12 is formed in a bottomed rectangular parallelepiped shape whose upper surface is open, and the upper case 14 functions as a closing member that closes the open upper surface. From above, it is formed in a substantially rectangular parallelepiped shape that is fitted so as to cover the outer periphery thereof. That is, the upper case 14 is formed to have a slightly larger size than the lower case 12 so as to be fitted.

2-3: Reinforcing frame preparation step After a filling step described later, as shown in FIG. 2A, the outer periphery of the case 10, specifically, a reinforcing frame 16 for reinforcing the outer peripheral surface in a posture during rolling is prepared. Is done. Here, the orientation of the case 10 during rolling means that the longitudinal direction of the case 10 (in the case where the case has a square shape, any central axis) is along the rolling direction, and the extending surface thereof is horizontal. It means posture along the direction.

  The reinforcing frame 16 includes first and second reinforcing members 16A and 16B that are fixed to both side plates 14A and 14B along the rolling direction of the upper case 14 in a state of extending along the rolling direction, respectively. 3rd and 4th reinforcement member 16C, 16D each fixed to the front board 14C and backplate 14D orthogonal to the rolling direction of this upper case 14 in the state extended along the direction orthogonal to a rolling direction is provided. Configured.

  Here, as for the 1st and 2nd reinforcement members 16A and 16B, the both ends along the rolling direction of the side plates 14A and 14B of the upper case 14 to which the respective first and second reinforcing members 16A and 16B are attached extend forward and backward than the corresponding side plates 14A and 14B, respectively. It is formed so as to have a length of The third and fourth reinforcing members 16C and 16D have the same length as the length of the front plate 14C and the rear plate 14D of the upper case 14 to which the third and fourth reinforcing members 16C and 16D are attached, respectively, in the direction orthogonal to the extending direction. It is formed and fixed or fixed to the first and second reinforcing members 16A and 16B.

2-4: Filling Step Next, the lower case 12 is filled with the mixed material M adjusted in the mixed material preparation step described above. This filling process is performed by the operation of uniformly feeding the mixed material M. At this time, tapping, that is, mechanical stuffing operation is performed on the lower case 12 simultaneously with the uniform charging operation to increase the packing density as powder. By this tapping, the theoretical filling rate of the mixed material is in the range of 35% to 65%.

  Specifically, as shown in FIG. 3A, the lower case 12 is placed at a predetermined filling position with the upper surface opened. Next, as shown in FIG. 3B, the extension sleeve 20 is overlaid on the lower case 12. Here, the extension sleeve 20 has a sleeve body 20A having a lower edge closely attached to the upper edge of the lower case 12 over the entire circumference in a state of being superimposed on the lower case 12, and a lower edge of the sleeve body 20A. A skirt portion 20B that is integrally formed on the outer periphery of the lower case 12 and is fitted on the outer periphery of the lower case 12 from the outside in a state of being overlaid on the lower case 12. ing.

  In this manner, with the extension sleeve 20 overlaid on the lower case 12, as shown in FIG. 3C, the mixed material M is poured into the space where the lower case 12 and the extension sleeve 20 are overlapped.

  Thereafter, the lower case 12 and the extension sleeve 20 are tapped while the mixed material M is put therein. As a result, as shown in FIG. 3D, in the space where the lower case 12 and the extension sleeve 20 are overlapped with each other, the mixed material M is increased in its packing density. The top surface will be lowered.

  Then, when a predetermined tapping time has elapsed and the mixed material M reaches a desired packing density, the tapping is stopped and the extension sleeve 20 is lifted upward. As a result, as shown in FIG. 3E, the mixed material M remains in the lower case 12 in a state of being made dense and maintaining its shape. As shown in the figure, the mixed material M remaining in the lower case 12 is in a state where the portion located in the extension sleeve 20 protrudes above the lower case 12.

  Thereafter, by moving the scraper 22 along the upper edge of the lower case 12, the portion of the mixed material M protruding above the lower case 12 is scraped sideways, as shown in FIG. The mixed material M that has been worn out is collected in the collection box 24. The mixture M collected in the collection box 24 is later returned to the blender described above, stirred again, and reused.

  On the other hand, by being worn out in this manner, the lower case 12 is fully filled with the mixed material M in a state where the filling density is increased. In other words, the upper surface of the mixed material M filled in the lower case 12 is flush with the upper edge of the lower case 12.

  Thereafter, as shown in FIG. 3G, the upper case 14 is fitted to the lower case 12 from above, and the open upper surface of the lower case 12 is closed, as shown in FIG. The to-be-rolled body 18 filled with full is comprised.

  Here, the state of the to-be-rolled body 18 shown in FIG. 3H is extremely as a “material” (meaning a material to be rolled in the rolling process described later) for producing the metal matrix composite of the present invention. It has important meaning. That is, although details will be described later, in the three-layer clad structure obtained by rolling the rolled body 18, the bottom plate 12E of the lower case 12 defines the lowermost layer, the mixture M defines the intermediate layer, The upper plate 14E of the upper case 14 defines the uppermost layer.

  In order for this three-layer clad structure to exhibit sufficient mechanical properties, adjacent layers need to be in close contact with each other. In the present invention, the lower surface of the mixture M and the lower case 12 The state where the upper surface of the mixture M and the lower surface of the upper plate 14E of the upper case 14 are in close contact with each other is achieved in the same manner as the upper surface of the bottom plate 12E is in close contact with the entire surface. Yes. As a result, in the three-layer clad structure after rolling, adjacent layers are rolled in close contact with each other, thereby being firmly bonded to each other. Is fully secured.

  Next, the work of reinforcing the object to be rolled 18 with the reinforcing frame 16 is performed. As shown in FIG. 2B, this reinforcing work is performed by surrounding the outer periphery excluding the upper and lower surfaces of the rolled body 18 in the rolling posture with a reinforcing frame 16.

  Specifically, the first and second reinforcing members 16A and 16B are connected to the side surfaces 14A and 14B to which the upper case 14 is attached, respectively, and both ends (that is, the front end and the rear end) along the rolling direction correspond to the side surfaces 14A. , 14B are temporarily fixed in a state of extending forward and backward. Next, both ends of the third reinforcing member 16C abut on the front end portions along the rolling direction of the first and second reinforcing members 16A and 16B, respectively, and both ends of the fourth reinforcing member 16D are the first ends. And temporarily fix | stop in the state which each contact | abuts to the rear-end part along the rolling direction of 2nd reinforcement member 16A, 16B.

  In a state where the reinforcing frame 16 is temporarily fixed to the rolled body 18 as described above, the rolled body 18 is put into a vacuum furnace, depressurized at a predetermined degree of vacuum, and degassed.

  After the degassing operation is completed, the temporarily fixed reinforcing frame 16 is fixed to the rolled body 18 by MIG welding. In this MIG welding, the upper edge of the reinforcing frame 16 and the upper edge of the upper case 14 are welded over the entire circumference, and the lower edge of the reinforcing frame 16 and the lower edge of the upper case 14 are welded over the entire circumference. To implement. Here, the lower edge of the upper case 14 and the lower edge of the lower case 12 are closely adjacent to each other. As a result, when the lower edge of the reinforcing frame 16 and the lower edge of the upper case 14 are welded, the lower edge of the lower case 12 is also welded together. As a result, the case 10 is hermetically sealed as a whole. It will be.

  Here, since the case 10 is hermetically sealed, if air exists in the rolled material 18 (if it remains), this may remain as a defect. For this reason, air vents (not shown) are formed at the four corners of the upper surface of the upper case 14 so that air does not escape from the inside of the member to be rolled 18 and remain in the rolling process. In addition, the formation of this hole can also be expected to have an effect of removing the gas that has entered the rolled body 18 during welding.

2-5: Preheating process The to-be-rolled body 18 reinforced by the reinforcing frame 16 is preheated before rolling. This preheating is carried out in a heating furnace by leaving it in an air atmosphere in the range of 300 ° C. to 600 ° C. for 2 hours or more. Here, the preheating atmosphere is not limited to being performed in the air, but is preferably performed in an inert gas such as argon, and more preferably in a vacuum atmosphere of 5 Pa or less. Is to be done.

2-6: Rolling Step This rolling step is to perform a plastic working called rolling on the rolled body 18. First, the situation in which the rolled body 18 has a specific effect in the present invention will be described.

  In other words, the material to be rolled 18 to be subjected to the rolling process is in a state where the mixed material to be rolled remains in a powder form and is not solidified at all. That is, as before, before being subjected to rolling, it is preformed for the purpose of maintaining its shape, specifically, it is pre-molded into the desired shape by pressing or current-pressure sintering. The situation is not. In the to-be-rolled body 18 in this invention, although the filling rate is raised by the above-mentioned tapping, it is not a thing to the extent of solidification but the state as a powder is maintained.

  Further, when being used in the rolling process, the upper and lower sides of the mixed material M as a powder are sandwiched between aluminum materials. Specifically, the upper surface of the mixed material M is covered entirely and tightly by the top plate portion 14E of the upper case 14, and the lower surface of the mixed material M is the bottom plate portion of the lower case 12. 12E is covered entirely and closely. Thus, this to-be-rolled body 18 is a plate-like clad material as a three-layer clad structure in which the mixed material M is filled in the case 10 and sealed, and the mixed material M is sandwiched between the upper and lower aluminum plates. "Material" is specified.

  The pre-rolled material 18 is rolled and formed into a target shape. When producing a plate-like clad material, it is also possible to obtain a clad plate material having a predetermined clad rate with an Al plate material or an Al container only by cold rolling. One processing may be performed by hot plastic processing, or a plurality of processing may be combined. Further, cold plastic working may be performed after hot plastic working. In the case of performing cold plastic working, if annealing is performed at 300 to 600 ° C. (preferably 400 to 500 ° C.) before the processing, the processing becomes easy.

  Since the to-be-rolled body 18 is clad with the aluminum plate, there are no ceramic particles on its surface that become the starting point of fracture during plastic working or wear dies. Therefore, it is possible to obtain an aluminum composite material having good rolling workability and excellent strength and surface properties. Further, the obtained hot plastic working material is clad with a metal and has good adhesion between the metal on the surface and the internal mixed material M. Therefore, the corrosion resistance is higher than that of an aluminum composite whose surface is not clad with a metal material. Excellent in impact resistance and thermal conductivity.

  In another preferred embodiment, it is also effective to cover the surface of the object to be rolled 18 with a metal protective plate, for example, a thin plate made of SUS or Cu before rolling. As a result, it is possible to prevent cracks and cracks in the front-rear direction that may occur during plastic processing.

  More specifically, the rolling process is more specifically performed by performing hot rolling by repeatedly performing 10 to 14 passes in a range of a rolling reduction of 10 to 70%. The rolling temperature in this hot rolling is set to 500 ° C.

  In addition, you may finish to a desired final thickness by this hot rolling. Moreover, you may perform warm rolling in the range of 200 to 300 degreeC after this hot rolling. Further, after this warm rolling, the second warm rolling may be performed at a temperature of 200 ° C. or lower.

  And after a rolling process is complete | finished, the heat processing process of the predetermined time in the range of 300 to 600 degreeC, ie, an annealing process, is implemented. After this annealing process, a cooling process is performed, a correction process is performed to a desired flatness, and both side edges, leading edge, and trailing edge are cut off to obtain a predetermined product shape (as a metal matrix composite). Plate clad material).

  Hereinafter, the manufacturing method of the metal matrix composite in the first embodiment will be described in detail with reference to the following various examples. In addition, the measuring method of each physical property value described in each example is as follows.

(1) Composition The composition of each material was analyzed by ICP emission spectroscopy.

(2) Average particle diameter The product name “Microtrack” (manufactured by Nikkiso) was used, and the measurement was performed by a laser diffraction particle size distribution measurement method. The average particle diameter is a volume-based median diameter.

(3) Rollability The presence or absence of cracks and surface properties when the sample was rolled were evaluated. Those with surface cracks on the plate surface, and those with no cracks on the surface, but with wrinkled irregularities were marked with “x”, and those without surface cracks or irregularities were marked with “◎”. .

(4) Microstructure observation The small piece which cut | disconnected the sample was embedded in resin, emery polishing and buffing were performed, and the structure | tissue was observed with the optical microscope.

(5) Neutron transmission test When protons accelerated by cycloton collide with a Be target, fast neutrons are generated by the ⁹ Be (p, n) ⁹ B reaction. Thereafter, the fast neutrons are converted into thermal neutrons by an energy moderator, and then irradiated to the metal matrix composite of the present invention as a parallel beam. At the time of this irradiation, if gold foil (diameter 10 mm, weight 200 mg, purity 99.997%) is placed on the front and back of the metal matrix composite, the gold foil is activated by the ¹⁹⁷ Au (n, γ) ¹⁹⁸ Au reaction. To do. The neutron transmittance is determined from the ratio of the activation rates of the two gold foils. FIG. 4 shows a calibration curve between ¹⁰ B area density (mg / cm 2) and neutron transmittance. (This calibration curve was created at Sumiju Test Inspection Co., Ltd., which conducts a neutron transmission test, based on the request of the present inventor.)
(6) SEM imaging Using an electron microscope (model JSM-5400) manufactured by JEOL Ltd., imaging was performed at an acceleration voltage of 10 kV.

A mixed material M was prepared by uniformly mixing an aluminum alloy powder having the composition shown in Table 1 with B ₄ C ceramic powder so as to be 30% by mass. The average particle size (D50) of the aluminum alloy powder was 10 μm, and the average particle size (D50) of the B ₄ C ceramic powder was 33 μm.

Subsequently, a lower square 12 made of an aluminum alloy (A5052) with a plate thickness of 3.0 mm, having a planar square shape with one side of 367.7 mm and an outer dimension of 54.8 mm in height, is prepared. An upper case 14 made of an aluminum alloy (A5052) having a plate-like square shape with a side of 370.9 mm and a substantially rectangular parallelepiped shape having an external dimension of 57.8 mm in height was prepared. The tensile strength of A5052 was 195 Mpa. The composition of the aluminum alloy (A5052) is shown in Table 1 below.

  As the first and second reinforcing members 16A and 16B constituting the reinforcing frame 16, aluminum having a thickness of 3.0 mm so as to exhibit outer dimensions of a length of 409.9 mm, a width of 20.0 mm, and a height of 57.8 mm. A plate (made of aluminum alloy A5052) was prepared by processing into an L-shaped cross section. Further, the third and fourth reinforcing members 16C and 16D constituting the reinforcing frame 16 have a thickness of 3.0 mm so as to exhibit external dimensions of a length of 370.9 mm, a width of 19.5 mm, and a height of 57.8 mm. The aluminum plate was processed and prepared to have an L-shaped cross section. The material of the reinforcing frame 16 was the same as that of the lower case 12 and the upper case 14 (JIS A5052P).

  Tapping was performed in a state where the above-described mixed material M was put in the lower case 12. Here, the tapping conditions were vibration period: 0.53 Hz, amplitude: 50 mm, input weight of 15.2 to 24.1 kg, and tapping time: 7 minutes or more.

The bulk density before tapping was 0.77 g / cm ³ . 5A to 5C show photographs obtained by SEM imaging of the surface state of the mixed material M before tapping (each figure is a photograph taken by magnifying the same mixed material M at different positions at a magnification of 750 times). Is shown.)
Moreover, the bulk density after tapping was 1.36 g / cm ³ . 6A to 6C show photographs obtained by SEM imaging of the surface state of the mixed material M after tapping (each figure is a photograph of the same mixed material M taken at different positions at a magnification of 750 times). Is shown.)
This result clearly confirms that the tapping increased the bulk density and increased the packing density by about 77%.

  Then, from the tapped state as described above, the protruding portion of the mixed material M rising upward from the lower case 12 is scraped off, and the mixed material M is fully filled in the lower case 12. Become. In this state, the upper case 14 is fitted from the upper side of the lower case 12, and the to-be-rolled body 18 is assembled. In addition, the height of this to-be-rolled body will be 57.8 mm.

Next, the obtained rolled material 18 is preheated at 500 ° C. for 2 hours or more, and using a two-stage rolling mill (400 Kw, Φ870 × 900), 11 passes at a rolling start temperature of 500 ° C. and an end temperature of 100 ° C. Then, it rolled to plate | board thickness 5.7mm. After this rolling, it was annealed at 450 ° C. for 4 hours and cooled at 200 ° C. The specific contents of the 11 passes are as shown in Table 2 below.

  A test piece was collected from the thus obtained three-layer clad material (final product), and the metal structure was observed with an optical microscope. 7 to 10 show micrographs thereof. Here, FIG. 7 is a (100 times) micrograph of a region including a portion where the top plate portion 14E of the upper case 14 appears as an upper skin layer, and FIG. 8 further shows the portion shown in FIG. It is the microscope picture which expanded and image | photographed (400 times). On the other hand, FIG. 9 is a microphotograph (100 times) of the intermediate region where the mixed material M is rolled, and FIG. 10 is a microphotograph of the portion shown in FIG. 9 further magnified (400 times). It is.

  It can be seen from the photographs shown in FIGS. 9 and 10 that the test piece is rolled to a sufficiently high density. 7 and 8 show that the upper skin layer formed from the upper plate 14E of the upper case 14 and the internal mixed material M are firmly adhered (joined). Needless to say, the lower skin layer formed from the bottom plate 12E of the lower case 12 and the internal mixed material M are firmly adhered (joined) as in the case of the upper skin layer.

In addition, the theoretical density ratio of the intermediate region (that is, the region where the mixed material M is rolled and solidified) in the final product (three-layer clad material) is measured by the specific gravity by the Archimedes method, and the theoretical density ratio is calculated from the measured specific gravity result. As shown in Table 3 below, the average value of the three samples is 99%, which is a high density that could not be achieved with the conventional product (theoretical density ratio: in calculating the measured density) Density ratio).

  Here, samples A, B, and C are three samples created at different dates and times in a state in which the same method as the manufacturing method of Example 1 described above is performed (the same applies hereinafter).

  In addition, as a general requirement specification value in the market where neutron absorbers are distributed, 97% or more is required in the intermediate layer, but the value of 99% which is the measurement result of the theoretical density ratio described above is It is sufficiently satisfied with the required specifications.

In addition, as described above, such a high theoretical density ratio is a result of being able to increase the filling density of the mixture M filled therein as much as possible by tapping when the rolled body 18 is produced. is there. As a result, the value of ¹⁰ B area density, which will be described later, is increased, and a desired neutron absorption rate can be achieved in a state where commercially available B ₄ C is used without using expensive concentrated boron.

  On the other hand, as a result of achieving such a high theoretical density ratio, it is possible to achieve a desired neutron absorption rate without keeping the cladding ratio low and taking a large intermediate layer made of the mixed material M. Combined with the fact that it is not necessary to use concentrated boron, the industrial applicability is greatly enhanced.

Furthermore, when the clad rate of the final product was measured, it was 16.8%. Here, the cladding ratio is a value expressed as a ratio of the total thickness of the upper and lower skin layers to the total thickness. Further, when the ¹⁰ B area density of the final product is calculated under the conditions of the plate thickness of 5.7 mm and the cladding ratio of 16.8%, it is 46.9 mg / cm ^2, and the calculation formula is as follows. is there.

General formula: Plate thickness (cm) × B ₄ C containing layer ratio / 100 (%) × 30% B ₄ C containing layer theoretical density (g / cm ³ ) × B ₄ C layer containing layer actual bulk density / theoretical density Ratio / 100 (%) × B ₄ C content average value / 100 (%) × boron content in B ₄ C / 100 (%) × ¹⁰ B content in boron / 100 (%) × variation rate / 100 (%)
It becomes.

Here, the ratio of the B ₄ C-containing layer is a ratio defined by (100−cladding ratio), and in this example, the cladding ratio is 16.8%, so that it is 83.2%. In this example, the variation rate was set to 90% in consideration of variations in the purity of B ₄ C, the plate thickness, the cladding rate, and the like.

If the numerical values of the present embodiment are applied to the above general formula,
¹⁰ B area density = (0.57) × (83.2 / 100) × (2.64) × (99/100) × (30/100) × (78/100) × (18.4 / 100) × (90/100) = 0.469 g / cm 2 = 46.9 mg / cm ²
Become
Here, the validity of the ¹⁰ B area density value being 47.9 mg / cm ² is verified.

First, as a neutron absorption rate in the market where neutron absorbers are distributed, 90% or more is required as a general requirement specification value. Since this neutron absorption rate of 90% is synonymous with neutron transmission rate of 10% (neutron absorption rate = 100−neutron transmission rate), when the ¹⁰ B area density for achieving neutron transmission rate of 10% is obtained, FIG. From the calibration curve shown in FIG. 5, it is found that the ¹⁰ B area density is 40 mg / cm ² . That is, it ¹⁰ B area density value as a measurement result is 47.9 mg / cm ^2, from 40 mg / cm ² required to achieve 90% or more, which is the required specification values as a neutron absorption rate However, it was proved that it was sufficiently high and sufficiently satisfied with this required specification.

  Here, the optimum range of the cladding ratio will be verified.

As described above, the clad rate is an important factor for achieving the required neutron absorption rate in relation to the ¹⁰ B surface density.

  Therefore, the thickness of the lower plate 12E of the lower case 12 and the thickness of the upper plate 14E of the upper case 14 are appropriately selected while the plate thickness is kept constant at 5.7 mm, as in the above-described embodiment. Then, the clad rate was selected from 5% to 35%, as shown in Table 4 below, so that a total of 9 types were selected, and a final product as a neutron absorber was prepared.

In Table 4, the symbol “◯” in the evaluation column indicates that the evaluation is satisfied, the symbol “×” indicates that the evaluation is not satisfied, and the symbol in the comprehensive evaluation column “◎” indicates a case where the overall evaluation is satisfied, and a symbol “×” indicates that the overall evaluation is not satisfied.

Then, the ¹⁰ B area density corresponding to each cladding value is calculated from the above general formula, and the neutron transmittance corresponding to each ¹⁰ B area density is derived from the calibration curve shown in FIG. When the absorptance was calculated and a condition where the neutron absorptivity was 90% or more was added as a threshold value, it was found that a cladding ratio exceeding 30% was not possible.

  On the other hand, when the rollability was visually confirmed in the process of manufacturing the final product, it was found that defective products such as cracks occurred in the final product having a thin skin layer with a cladding rate of up to 13%. Therefore, it has been found that, from the viewpoint of rollability, a cladding ratio of 13% or less is not possible.

  Considering the evaluation results of both of the above, it has been found that the optimum range of the cladding ratio is 15% or more and 25% or less.

In addition, the mechanical properties of the final product are determined by using a known mechanical property tester, tensile strength (σ _B ), 0.2% proof stress (σ _0.2 ), elongation (δ), and physical properties. The thermal conductivity as a value was measured respectively. In this measurement test, the values of the three samples were measured, and the average value of each was determined. The results were as shown in Table 5 below.

Here, regarding the tensile strength (σ _B ) in the market where neutron absorbers are distributed, 35 MPa or more is required as a general requirement specification value. Compared with this required specification value, the final product has a tensile strength (σ _B ) of 168 MPA on average, which is about 5 times higher, and has sufficient tensile strength. There was found.

In addition, in order to investigate the correlation between the ¹⁰ B area density, the tensile strength, and the neutron absorption rate of the neutron absorber in this example, the value of the ¹⁰ B area density was varied to determine the tensile strength at each value. Neutron absorption rate was measured.

  The result is shown in FIG.

As is apparent from FIG. 11, in order to achieve the neutron absorption rate exceeding 90%, it is essential that the ¹⁰ B area density is 40 mg / cm ² or more, and the ¹⁰ B area density is If it is 40 mg / cm ² or more, a tensile strength of 110 MPa or more is essential, but if the ¹⁰ B area density is in the range of 40 mg / cm ² to 50 mg / cm ² , both conditions are satisfied. It has been found.

That is, the neutron absorber of the present invention has a neutron absorption rate of 90% or more and a tensile strength of 110 MPa or more when the ¹⁰ B area density is in the range of 40 mg / cm ² to 50 mg / cm ^2. In addition to satisfying the specifications required by the market, it also exhibits the performance of achieving higher values.

Further, regarding 0.2% proof stress (σ _0.2 ) in the market where neutron absorbers are distributed, 50 MPa or more is required as a general required specification value. Compared to this required specification value, the 0.2% yield strength (σ _0.2 ) of the final product is 151 MPA as an average value, which is an extremely high value of about three times, which is a sufficient 0.2 It was found to have% proof stress.

  Furthermore, with respect to the growth (δ) in the market where neutron absorbers are distributed, the general requirement specification value is required to be 0.5% or more. Compared with this required specification value, the final product elongation (δ) is 3.9% as an average value, which is about 8 times as high as the average value. did.

  Thus, the neutron absorber as the metal matrix composite according to the present invention exhibits a considerably higher value than the specification value required by the market in terms of its mechanical strength. It has been found that it has mechanical strength and therefore has high industrial applicability.

  On the other hand, regarding the thermal conductivity in the market where neutron absorbers are distributed, the general requirement specification value is required to be 60 W / m · K or more. Compared with this required specification value, the thermal conductivity of the final product is 103 W / m · K as an average value, which is about 1.5 times higher, and has a sufficient thermal conductivity. It has been found.

  Thus, the neutron absorber as the metal matrix composite according to the present invention exhibits a value considerably higher than the specifications required by the market in terms of its mechanical strength and thermal conductivity. It has been found that it has sufficient mechanical strength and thermal conductivity, and therefore has very high industrial applicability.

The first embodiment described above is described based on the embodiment in which the base material of the mixed powder M includes B ₄ C ceramic particles and aluminum powder, but the base material used in the manufacturing method of the present invention is as follows. Needless to say, the composition is not limited to such a composition. The main composition of the base material is not limited to aluminum, and other suitable metal powders such as copper, magnesium, titanium, gallium, iron, and indium can be used.

  In the above, various useful examples of the present invention have been shown and described. The present invention is not limited to the various embodiments and modifications described above, and various modifications can be made without departing from the gist of the present invention and the contents described in the appended claims. There is no.

  The metal matrix composite material of the present invention is used for a shielding material having neutron absorption performance for a nuclear power generation spent fuel body storage tank or the like.

12 Lower case 14 Upper case 18 Rolled object 20 Sleeve 22 Scraper 24 Recovery box M Mixed material

Claims (4)

A pair of metal plates with a mixed material sandwiched between them, the mixed material comprising metal powder and ceramic particles having a neutron absorbing function, and a theoretical density ratio of an intermediate layer composed of the mixed material is 98% The percentage of the total thickness of both metal plates in the total thickness is a method for producing a metal matrix composite having a range of 15% to 25%,
(A) mixing the metal powder and the ceramic particles to prepare a mixed material;
(B) preparing a metal case having a lower case and an upper case formed to be sealable on the lower case;
(C) In a state where a sleeve main body that is in close contact with the upper edge of the lower case is overlapped on the lower case, the mixed material is introduced, and after tapping, the sleeve main body is lifted upward, Filling the upper case with the upper edge of the lower case by moving a scraper along the upper edge of the lower case ;
(D) providing a rolled body from the metal case filled with the mixed material by sealing the upper case over the lower case; and
(E) a step of preheating the rolled body so that the mixed material maintains a powder state;
(F) cold rolling the to-be-rolled body preheated in the preheating step to obtain a metal composite material, and a method for producing a metal matrix composite material. The metal plate is made of aluminum or stainless steel,
The metal powder is aluminum powder,
The method for producing a metal matrix composite according to claim 1, wherein the ceramic particles include B ₄ C particles. An intermediate layer comprising metal powder and ceramic particles having a neutron absorption function, a metal first skin layer formed in close contact with one surface of the intermediate layer, and the other surface of the intermediate layer A metal second skin layer formed in close contact, the theoretical density ratio of the intermediate layer is 98% or more, and the total thickness of the first and second skin layers is The percentage of the total thickness is a method for producing a metal matrix composite having a range of 15% or more and 25% or less,
(A) mixing the metal powder and the ceramic particles to prepare a mixed material;
(B) preparing a metal case having a lower case and an upper case formed to be sealable on the lower case;
(C) In a state where a sleeve main body that is in close contact with the upper edge of the lower case is overlapped on the lower case, the mixed material is introduced, and after tapping, the sleeve main body is lifted upward, Filling the upper case with the upper edge of the lower case by moving a scraper along the upper edge of the lower case ;
(D) providing a rolled body from the metal case filled with the mixed material by sealing the upper case over the lower case; and
(E) a step of preheating the rolled body so that the mixed material maintains a powder state;
And (f) cold rolling the rolled body preheated in the preheating step to obtain a metal composite material. A method for producing a metal matrix composite material, comprising: The metal powder is aluminum powder,
The ceramic particles include B ₄ C particles,
The method for producing a metal matrix composite according to claim 3, wherein the skin layer is made of aluminum or stainless steel.