JP2007040914A - Aluminum powder alloy composite for absorbing neutron, manufacturing method therefor, and basket manufactured using the same - Google Patents
Aluminum powder alloy composite for absorbing neutron, manufacturing method therefor, and basket manufactured using the same Download PDFInfo
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Abstract
Description
本発明は、中性子吸収能に優れたアルミニウム粉末合金複合材及びその製造方法に関する。また、本発明は、使用済み核燃料の輸送や貯蔵等に用いられるキャスクのバスケットにも関する。 The present invention relates to an aluminum powder alloy composite material excellent in neutron absorption ability and a method for producing the same. The present invention also relates to a basket of cask used for transportation and storage of spent nuclear fuel.
核燃料は、使用済みのものでも高速又は熱中性子を発生させている。この中性子は核反応を促進させるので、多くの核燃料をまとめて置いておくと、核反応が中性子により進んでしまう。そのため、核燃料を輸送したり貯蔵したりする場合には、一般にバスケットと呼ばれる中性子吸収材を周りに溶接したステンレスの角パイプやホウ素等の中性子吸収元素を含有するステンレス角パイプの集合体のなかに、小分けして収納している。バスケットは、キャスクと呼ばれる容器の中に納められ、その状態で、輸送や貯蔵が行われている（例えば、特許文献１参照）。 Nuclear fuels, even those that have been used, generate fast or thermal neutrons. Since this neutron promotes the nuclear reaction, if many nuclear fuels are put together, the nuclear reaction will be advanced by the neutron. Therefore, when transporting or storing nuclear fuel, it is generally a stainless steel square pipe welded around a neutron absorber called a basket or a collection of stainless steel square pipes containing neutron absorbing elements such as boron. It is stored in small portions. The basket is stored in a container called a cask and is transported and stored in that state (see, for example, Patent Document 1).
一般に、中性子吸収能を備えた物質としては、Ｇｄ、Ｓｍ等が挙げられるが、前述の中性子吸収材にはホウ素が最も良く用いられている。Ｂを用いた中性子吸収材としては、「ボラール（Ｂｏｒａｌ）」と称する、アルミニウム板二枚の間にサンドイッチ状にＢ４Ｃとアルミニウム粉末を混合した混合粉末を挟み込み圧延した板状の成形体が従来から使用されており、この中性子吸収材をステンレスなどの角パイプに溶接し、バスケットを製造していた。 In general, examples of the substance having neutron absorption ability include Gd, Sm, and the like. Boron is most often used for the above-described neutron absorber. As a neutron absorber using B, there is a plate-like molded body obtained by sandwiching and rolling a mixed powder obtained by mixing B 4 C and aluminum powder in a sandwich shape between two aluminum plates, called “Boral”. Conventionally, baskets are manufactured by welding this neutron absorber to a square pipe such as stainless steel.
しかして、近年軽量化の要望等があり、ＪＩＳ規格のアルミニウム粉末とホウ素又はホウ素化合物粉末を混合して加圧焼結した使用済み核燃料集合体貯蔵用容器のバスケット材が提案されるようになってきた（例えば、特許文献２、３参照）。
また、他の中性子吸収用成形体として、ホウ素をアルミニウム合金中に溶解させ製造した中性子吸収体も提案されている（例えば、特許文献４参照）。
As another neutron absorption molded body, a neutron absorber manufactured by dissolving boron in an aluminum alloy has also been proposed (see, for example, Patent Document 4).
キャスクのバスケット材には、使用済み核燃料棒の貯蔵中常に２００℃前後の高温にさらされるため、高温での強度や高温からの連続的冷却時での材料軟化性の抵抗、すなわち耐熱性及び耐食性が要求される。しかし母材となるアルミニウム合金がＪＩＳ規格の合金であると十分な強度や耐食性を得ることが難しかった。
また、ホウ素をアルミニウム合金中に溶解させた溶製材である中性子吸収材は、ホウ素を溶解するのが難しく、ホウ素の濃度を高めることができなかった。更にホウ素を溶解させるためにはアルミニウム合金を８００℃以上まで加熱する必要があり、生産性が悪く、溶解炉も傷みやすいという問題があった。また、ホウ素を均一に分散させることが難しく、品質的にバラツキが生じやすいという問題もあった。
Cask basket materials are always exposed to high temperatures around 200 ° C during storage of spent nuclear fuel rods, so strength at high temperatures and resistance to material softening during continuous cooling from high temperatures, ie heat resistance and corrosion resistance Is required. However, if the aluminum alloy used as the base material is a JIS standard alloy, it has been difficult to obtain sufficient strength and corrosion resistance.
In addition, a neutron absorber, which is a smelting material in which boron is dissolved in an aluminum alloy, is difficult to dissolve boron, and the concentration of boron cannot be increased. Further, in order to dissolve boron, it is necessary to heat the aluminum alloy to 800 ° C. or higher, and there is a problem that the productivity is poor and the melting furnace is easily damaged. In addition, there is a problem that it is difficult to uniformly disperse boron, and quality tends to vary.
本発明は、上記事情に鑑みてなされたもので、高温強度や耐食性に優れた中性子吸収用アルミニウム合金複合材を提供することを目的とする。
また本発明は、高温強度や耐食性に加えて、更に熱伝導性も良好な中性子吸収用アルミニウム合金複合材を提供することを目的とする。
更に本発明は、上述の中性子吸収用アルミニウム複合材を安価に製造できる生産性に優れた製造方法を提供することを目的とする。
また本発明は、上述の中性子吸収用アルミニウム複合材を用いて製造されたキャスクのバスケットを提供することも目的とする。
This invention is made | formed in view of the said situation, and it aims at providing the aluminum alloy composite material for neutron absorption excellent in high temperature strength and corrosion resistance.
Another object of the present invention is to provide a neutron-absorbing aluminum alloy composite material that has good thermal conductivity in addition to high-temperature strength and corrosion resistance.
Furthermore, an object of the present invention is to provide a production method excellent in productivity that can produce the above-described aluminum composite for neutron absorption at low cost.
Another object of the present invention is to provide a cask basket manufactured using the above-described neutron absorbing aluminum composite.
本発明の中性子吸収用アルミニウム粉末合金複合材は、アルミニウム合金からなる母材中に中性子吸収能を有するホウ素系化合物が分散せしめられてなる中性子吸収用アルミニウム粉末合金複合材であって、母材を、母材の全質量に対して０．８〜３質量％のＭｎ、０．１５〜１．５質量％のＭｇ、０．１〜０．６質量％のＣｕ、０．１〜１．０質量％のＦｅを含み、残部がアルミニウムと不可避不純物からなるアルミニウム合金としたことを特徴とする。 The aluminum powder alloy composite material for neutron absorption according to the present invention is an aluminum powder alloy composite material for neutron absorption in which a boron-based compound having neutron absorption ability is dispersed in a base material made of an aluminum alloy. , 0.8-3 mass% Mn, 0.15-1.5 mass% Mg, 0.1-0.6 mass% Cu, 0.1-1.0 based on the total mass of the base material An aluminum alloy containing mass% Fe and the balance being aluminum and inevitable impurities is used.
上記において、母材のアルミニウム合金は、更にＳｉを、母材の全質量に対して０．８〜２．０質量％含有させたものでも良い。また母材のアルミニウム合金には、Ｓｉと共に又はＳｉとは別に、更にＣｒを母材の全質量に対して０．０３〜１質量％含有させたものでも良い。
本発明において使用されるホウ素系化合物は、複合材の全質量に対してホウ素量で０．４〜２４質量％であることが好ましい。またホウ素系化合物の種類は、中性子吸収能に優れるものであれば如何なるものでも使用可能であるが、特にＢ４Ｃであることが好ましく、Ｂ４Ｃの場合、その含有量は好適には複合材の全質量に対して化合物量で０．５〜１０質量％である。
In the above, the aluminum alloy as the base material may further contain Si in an amount of 0.8 to 2.0 mass% with respect to the total mass of the base material. In addition, the base aluminum alloy may contain 0.03 to 1% by mass of Cr together with Si or separately from Si based on the total mass of the base material.
The boron compound used in the present invention is preferably 0.4 to 24% by mass in terms of boron based on the total mass of the composite material. Any boron compound may be used as long as it has an excellent neutron absorption ability, but B 4 C is particularly preferable. In the case of B 4 C, the content is preferably composite. The amount of the compound is 0.5 to 10% by mass with respect to the total mass of the material.
本発明の製造方法は、上記中性子吸収用アルミニウム粉末合金複合材の製造に特に適したもので、上述の組成を有する母材となるアルミニウム合金粉末と、ホウ素系化合物粉末、好適には平均粒径が１〜２０μｍ（更に好ましくは５〜１０μｍ）のＢ４Ｃ粉末を混合して混合粉末を生成した後、加圧成形し、減圧雰囲気、不活性ガス雰囲気あるいは還元性ガス雰囲気中で、３００〜５７０℃まで加熱し、脱ガス処理を行い、次に熱間塑性加工を行うことを特徴とする。
また、他の態様として、上述の組成を有する母材となるアルミニウム合金粉末と、ホウ素系化合物粉末、好適には平均粒径が１〜２０μｍ（更に好ましくは５〜１０μｍ）のＢ４Ｃ粉末を混合して混合粉末を生成した後、これをアルミニウム製の容器に封入し、ついで加圧成形し、減圧雰囲気、不活性ガス雰囲気あるいは還元性ガス雰囲気中で、３００〜５７０℃まで加熱し、脱ガス処理を行い、次に熱間塑性加工を行っても良い。
熱間塑性加工としては、熱間押出加工が好ましい。
更に、本発明に係る、使用済み核燃料を収容するキャスクのバスケットは、上述の本発明に係る中性子吸収用アルミニウム粉末合金複合材で製造したことを特徴とする。
The production method of the present invention is particularly suitable for the production of the above-mentioned neutron-absorbing aluminum powder alloy composite, which is an aluminum alloy powder serving as a base material having the above-described composition, a boron compound powder, and preferably an average particle size Is mixed with B 4 C powder of 1 to 20 μm (more preferably 5 to 10 μm) to form a mixed powder, which is then pressed and molded in a reduced pressure atmosphere, an inert gas atmosphere or a reducing gas atmosphere, It is characterized by heating to 570 ° C., degassing treatment, and then hot plastic working.
Further, in another embodiment, the aluminum alloy powder serving as a base material having the composition described above, boron-based compound powder, the average particle diameter preferably is a B 4 C powder 1 to 20 [mu] m (more preferably 5 to 10 [mu] m) After mixing to produce a mixed powder, it is sealed in an aluminum container, then press-molded, heated to 300-570 ° C. in a reduced-pressure atmosphere, inert gas atmosphere or reducing gas atmosphere, and removed. Gas treatment may be performed, and then hot plastic working may be performed.
As the hot plastic working, hot extrusion is preferable.
Further, the cask basket for containing spent nuclear fuel according to the present invention is manufactured by the above-described neutron-absorbing aluminum powder alloy composite material according to the present invention.
アルミニウム合金からなる母材中に中性子吸収能を有するホウ素系化合物が分散せしめられてなる中性子吸収用アルミニウム粉末合金複合材においては、所望の中性子吸収能を得るには一定量のホウ素系化合物を含有せしめることが必要であるが、ホウ素系化合物の添加量を増加させると、ホウ素系化合物はアルミニウム合金に比べて融点や硬度が非常に高いため、硬度等は向上するものの、焼結性、塑性加工性、伸び等が低下してしまう。そこで、複合材の高温強度、耐熱性、耐食性を高めるには、ホウ素系の添加量を増減させないで、母材となるアルミニウム合金を種々変更してみることが考えられる。しかしながら、例えば特許文献３にあるように、アルミニウム合金としてＪＩＳ規格の合金から所望の性質を具備すると思われる合金を選択しただけでは、十分な強度や耐食性を得ることができなかった。 A neutron absorbing aluminum powder alloy composite material in which a boron compound having neutron absorption ability is dispersed in a base material made of an aluminum alloy contains a certain amount of boron compound to obtain a desired neutron absorption ability. Although it is necessary to increase the amount of boron-based compound added, the boron-based compound has a very high melting point and hardness compared to the aluminum alloy, so the hardness is improved, but sinterability, plastic working Property, elongation, etc. will decrease. Therefore, in order to increase the high temperature strength, heat resistance, and corrosion resistance of the composite material, it is conceivable to variously change the aluminum alloy serving as a base material without increasing or decreasing the amount of boron-based additive. However, for example, as disclosed in Patent Document 3, sufficient strength and corrosion resistance could not be obtained simply by selecting an alloy that seems to have desired properties from an JIS standard alloy as an aluminum alloy.
そこで、本発明者等は、複合材の母材として用いた場合に、高温強度、耐熱性及び耐食性に優れた性質を有し、かつ強化材との密着性の良いアルミニウム粉末合金について、ＪＩＳ規格の合金にとらわれず、あらゆる添加元素を検討し、試行錯誤を繰り返して鋭意研究を重ねた結果、焼結性に優れるＡｌ−Ｍｎ−Ｍｇ−Ｃｕ−Ｆｅ系アルミニウム合金を母材とすると、意外にも高温強度、耐熱性、耐食性にも優れた複合材を得ることができることが分かった。
しかして、本発明に係るアルミニウム合金粉末複合材は、従来の複合材に比して、高温強度、耐熱性及び耐食性に優れる。
また、本発明の好適な実施態様では、母材と強化材の密着性がよく、強度も熱伝導性も良好なアルミニウム合金粉末複合材が得られる。
更に、本発明の製造方法は、ホウ素を溶解させることを要しないので、生産性が高く、安価に複合材を製造できるという効果を奏する。
Therefore, the present inventors, when used as a base material of a composite material, have a property excellent in high-temperature strength, heat resistance and corrosion resistance, and have good adhesion to a reinforcing material, and are JIS standard. As a result of investigating all additive elements and repeating trial and error regardless of the alloy of the alloy, and repeating the earnest research, it is surprising that the Al-Mn-Mg-Cu-Fe-based aluminum alloy having excellent sinterability is used as a base material. It was also found that a composite material excellent in high temperature strength, heat resistance and corrosion resistance can be obtained.
Therefore, the aluminum alloy powder composite material according to the present invention is superior in high temperature strength, heat resistance and corrosion resistance as compared with conventional composite materials.
Further, in a preferred embodiment of the present invention, an aluminum alloy powder composite material having good adhesion between the base material and the reinforcing material and good strength and thermal conductivity can be obtained.
Furthermore, since the manufacturing method of the present invention does not require dissolution of boron, the productivity is high and the composite material can be manufactured at low cost.
前述のように、本発明に係る中性子吸収用アルミニウム粉末合金複合材は、母材がＭｎ：０．８〜３．０質量％、Ｍｇ：０．１５〜１．５質量％、Ｃｕ：０．１〜０．６質量％、Ｆｅ：０．１〜１．０質量％を含み、残部がアルミニウムと不可避不純物からなり、適宜Ｓｉ：０．８〜２．０質量％、Ｃｒ：０．０３〜１質量％のいずれか１以上を添加するアルミニウム合金であり、中性子吸収材がホウ素系化合物である。以下、各元素の作用について説明する。 As described above, in the aluminum powder alloy composite for neutron absorption according to the present invention, the base material is Mn: 0.8 to 3.0% by mass, Mg: 0.15 to 1.5% by mass, Cu: 0.0. 1 to 0.6% by mass, Fe: 0.1 to 1.0% by mass, the balance is made of aluminum and inevitable impurities, Si: 0.8 to 2.0% by mass, Cr: 0.03 to It is an aluminum alloy to which any one or more of 1% by mass is added, and the neutron absorber is a boron-based compound. Hereinafter, the action of each element will be described.
［Ｍｎ：０．８〜３．０質量％］
Ｍｎは急冷凝固によってＡｌ中での固溶量が多くなり、また、Ａｌ中での拡散が遅く、母材の耐熱性、耐食性を向上させ、更に生成する化合物Ａｌ−Ｍｎ，Ａｌ−（Ｆｅ＋Ｍｎ）−Ｓｉもその微細化合物の存在によって耐熱性を改良する。
効果を生じる量は０．８質量％以上であり、３．０質量％を超えると変形抵抗が高くなり、熱間加工性を低下させる。
[Mn: 0.8 to 3.0% by mass]
Mn increases the amount of solid solution in Al due to rapid solidification, and also diffuses slowly in Al, improves the heat resistance and corrosion resistance of the base material, and further produces compounds Al—Mn, Al— (Fe + Mn). -Si also improves heat resistance due to the presence of its fine compounds.
The amount that produces the effect is 0.8% by mass or more, and if it exceeds 3.0% by mass, the deformation resistance becomes high and the hot workability is lowered.
［Ｍｇ：０．１５〜１．５質量％］
Ｍｇは、母相中に固溶したり、他の元素と化合物（Ｍｇ２Ｓｉ）を形成したりして、機械的強度や耐摩耗性を向上させる作用を呈する。この作用は、０．１５質量％以上で顕著となり、逆に１．５質量％を超えると熱間加工性や耐食性を低下させる。
また、Ｍｇは、アルミニウム合金の融点を低下させ、自身も高温拡散しやすい元素であるため、焼結性が向上する。更にセラミックス粒子とのアルミニウム合金の濡れ性を改善する作用もある。
[Mg: 0.15 to 1.5% by mass]
Mg exhibits a function of improving mechanical strength and wear resistance by forming a solid solution in the matrix or forming a compound (Mg 2 Si) with another element. This effect becomes remarkable at 0.15% by mass or more, and conversely when it exceeds 1.5% by mass, hot workability and corrosion resistance are lowered.
Further, Mg is an element that lowers the melting point of the aluminum alloy and easily diffuses at a high temperature, so that the sinterability is improved. Furthermore, it also has the effect of improving the wettability of the aluminum alloy with the ceramic particles.
［Ｃｕ：０．１〜０．６質量％］
Ｃｕは、Ａｌに対して固溶化して高温時の母材強度の維持に効果が有り、また他の元素同様にＭｎ系化合物の析出を促進する。一方、０．６％を越えると耐食性の低下、熱間加工での不良を生じやすくなる。
[Cu: 0.1 to 0.6% by mass]
Cu is solid-solved in Al and effective in maintaining the strength of the base material at high temperatures, and promotes the precipitation of Mn-based compounds like other elements. On the other hand, if it exceeds 0.6%, the corrosion resistance is lowered and defects in hot working are likely to occur.
［Ｆｅ：０．１〜１．０質量％］
Ｆｅは、Ａｌ−Ｆｅ−Ｃｕ系化合物、Ａｌ−（Ｆｅ，Ｍｎ）系化合物、Ａｌ−Ｆｅ−Ｓｉ系化合物、Ａｌ−（Ｍｎ，Ｆｅ）−Ｓｉ系化合物を形成し、耐熱性を向上させる。この効果は０．１質量％以上の添加で顕著となり、逆に１．０質量％を超えて添加されると耐食性、靭性低下の原因となる。また、押し出しなどの加工時に表面欠陥を生じやすくなる。
[Fe: 0.1 to 1.0% by mass]
Fe forms an Al—Fe—Cu based compound, an Al— (Fe, Mn) based compound, an Al—Fe—Si based compound, and an Al— (Mn, Fe) —Si based compound to improve heat resistance. This effect becomes prominent when added in an amount of 0.1% by mass or more, and conversely, if added over 1.0% by mass, the corrosion resistance and toughness are reduced. In addition, surface defects are likely to occur during processing such as extrusion.
［Ｓｉ：０．８〜２．０質量％］
Ｓｉは、他の元素と化合物（Ａｌ−Ｆｅ−Ｓｉ，Ａｌ−（Ｆｅ＋Ｍｎ）−Ｓｉ系化合物）を形成したりして、高温強度を向上させ、耐摩耗性を向上させる作用を呈する。この作用は０．８質量％以上で顕著となり、逆に２．０質量％を超えると過剰なＳｉが単独で存在し、伸びなどの延性低下を生じやすくなる。Ｓｉ添加の場合は、Ｍｇ量を低くして、Ａｌ−Ｍｎ−Ｓｉ系化合物を多量に析出させるとその効果は大きくなる。
Ｓｉは、アルミニウム合金の融点を低下させ、自身も高温拡散しやすい元素であるため、焼結性が向上する。
[Si: 0.8 to 2.0% by mass]
Si forms a compound (Al-Fe-Si, Al- (Fe + Mn) -Si-based compound) with other elements to improve the high-temperature strength and to improve the wear resistance. This effect becomes remarkable at 0.8% by mass or more, and conversely, when it exceeds 2.0% by mass, excess Si is present alone, and ductility such as elongation tends to be reduced. In the case of adding Si, the effect increases if the amount of Mg is lowered and a large amount of Al-Mn-Si compound is precipitated.
Since Si is an element that lowers the melting point of the aluminum alloy and easily diffuses at high temperatures, the sinterability is improved.
［Ｃｒ：０．０３〜１質量％］
Ｃｒは、Ｍｎと同一の効果を奏するので、０．０３〜１質量％含有させることが、好ましい。
[Cr: 0.03 to 1% by mass]
Since Cr has the same effect as Mn, it is preferable to contain 0.03 to 1% by mass.
［不可避不純物］
本発明の複合材の母材となるアルミニウム合金では、Ｚｎなどの不可避不純物は各元素で０．１質量％以下であれば耐食性などの性質に大きな影響を与えないので、不可避不純物として許容される。
[Inevitable impurities]
In the aluminum alloy which is the base material of the composite material of the present invention, inevitable impurities such as Zn are allowed to be inevitable impurities because they do not greatly affect properties such as corrosion resistance if each element is 0.1% by mass or less. .
［ホウ素系化合物］
本発明において用いて好適なホウ素系化合物は、中性子吸収能に優れるものであれば如何なるものでもよいが、好適には、例えば炭化ホウ素、酸化ホウ素、窒化ホウ素等、ホウ化アルミニウム等の金属とホウ素との化合物等を挙げることができ、これらを単独で又は混合物として使用することができる。特に、炭化ホウ素Ｂ４Ｃは、工業的に量産でき、中性子を良く吸収するＢの同位体であるＢ１０を約２０％含有するので複合化に最適である。
このホウ素系化合物は、前述のアルミニウム合金粉末に、ホウ素量で０．４〜２４質量％の量で含有せしめられる。０．４質量％以上とした理由は、０．４質量％より少ないと、十分な中性子吸収能力が得られないためであり、十分な中性子吸収能力を得るために中性子吸収材の板厚を厚くしなければならなくなり、限られたスペース内に中性子吸収成形体を収納することができなくなるばかりか、材料が嵩むという問題がある。また、２４質量％以下とした理由は、２４質量％より多いと、成形時の変形抵抗が高く、成形加工が難しい上、成形体が脆くなって、折れやすくなるという問題があるからである。またアルミニウムとホウ素化合物の密着性も悪くなり、空隙ができやすく、放熱性も低下する。例えば、Ｂ４Ｃの場合、前述のアルミニウム合金粉末に、化合物で０．５〜３０質量％含有せしめられる。０．５質量％未満では、中性子吸収材として十分に作用しない一方、３０質量％を超えると塑性加工性や切削性も悪化する。
[Boron compounds]
The boron-based compound suitable for use in the present invention may be any compound as long as it has an excellent neutron absorption capability. Preferably, for example, boron carbide, boron oxide, boron nitride, etc., a metal such as boron boride and boron And the like, and these can be used alone or as a mixture. In particular, boron carbide B 4 C can be industrially mass-produced and contains about 20% of B10, which is an isotope of B that absorbs neutrons well, and is therefore optimal for compounding.
This boron-based compound is contained in the aforementioned aluminum alloy powder in an amount of 0.4 to 24% by mass in terms of boron. The reason why it is 0.4% by mass or more is that if it is less than 0.4% by mass, sufficient neutron absorption capability cannot be obtained, and in order to obtain sufficient neutron absorption capability, the thickness of the neutron absorber is increased. There is a problem that not only the neutron absorption molded body cannot be stored in a limited space, but also the material is bulky. The reason why the amount is 24% by mass or less is that when the amount is more than 24% by mass, there is a problem that deformation resistance at the time of molding is high and molding is difficult, and the molded body becomes brittle and easily breaks. In addition, the adhesion between aluminum and the boron compound is deteriorated, voids are easily formed, and heat dissipation is also reduced. For example, in the case of B 4 C, the above-described aluminum alloy powder is contained in an amount of 0.5 to 30% by mass as a compound. If it is less than 0.5% by mass, it does not sufficiently act as a neutron absorber, whereas if it exceeds 30% by mass, plastic workability and machinability also deteriorate.
以下に、本発明の製造方法を説明する。
［第一の製造方法］
本発明の製造方法の第一の実施形態は、（ａ）上述の組成を有する母材となるアルミニウム合金粉末と、ホウ素系化合物粉末を混合して混合粉末を生成する工程と、（ｂ）上記混合粉末を加圧成形する工程と、（ｃ）加圧成形した成形体を所定雰囲気中で加熱し、脱ガス処理を行う工程と、（ｄ）最後に熱間塑性加工を行う工程とを具備する。以下、使用される原材料についてまだ述べていない特性等についての説明を追加した上で、各工程を（ａ）工程から（ｄ）工程の順に詳細に説明する。
Below, the manufacturing method of this invention is demonstrated.
[First production method]
In the first embodiment of the production method of the present invention, (a) a step of producing a mixed powder by mixing an aluminum alloy powder serving as a base material having the above-described composition and a boron-based compound powder, and (b) the above A step of pressure-forming the mixed powder, (c) a step of heating the pressure-formed molded body in a predetermined atmosphere to perform degassing treatment, and (d) a step of finally performing hot plastic working. To do. Hereinafter, after adding the description about the characteristics etc. which have not been described about the raw material used yet, each process is demonstrated in detail from the (a) process to the (d) process.
（１）原材料の説明
［母材のアルミニウム合金粉末］
Ｂ４Ｃ等の粒子と混合される合金の母材となるアルミニウム合金粉末の平均粒径は特に限定されるものではないが、上限値は一般には５００μｍ以下、好ましくは１５０μｍ以下、より好ましくは６０μｍ以下の粉末を用いることができる。平均粒径下限値は製造可能であれば特に限定されるものではないが、通常は１μｍ以上、好ましくは２０μｍ以上である。アルミニウム合金粉の粒度分布を１００μｍ以下として、ホウ素系化合物粒子の平均粒度を１０μｍ以下とするとホウ素系化合物粒子が均一に分散し、ホウ素系化合物粒子の希薄な部分が非常に少なくなり、特性の安定化に効果がある。アルミニウム合金粉末の平均粒径は、後述するＢ４Ｃ等の粒子の平均粒径の差が大きいと押出加工や圧延加工等の塑性加工の際に割れが生じやすいので、平均粒径の差を小さくすることが好ましい。平均粒径が大きくなりすぎると、平均粒径を大きくできない例えばＢ４Ｃ粒子との均一混合が困難となる一方、平均粒径が小さすぎると、微細アルミニウム合金粉末同士で凝集が起こり易くなり、Ｂ４Ｃ粒子等との均一混合が非常に困難になるからである。また、かかる範囲内の平均粒径とすることにより、一層優れた加工性、成形性、機械的特性を得ることもできる。
なお、本発明における平均粒径は、レーザー回折式粒度分布測定法による値を示す。粉末形状も限定されるものではなく、例えば涙滴状、真球状、回転楕円体状、フレーク状又は不定形状等いずれであっても差し支えない。
(1) Description of raw materials [base aluminum alloy powder]
The average particle size of the aluminum alloy powder that is the base material of the alloy mixed with particles such as B 4 C is not particularly limited, but the upper limit is generally 500 μm or less, preferably 150 μm or less, more preferably 60 μm. The following powders 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 1 μm or more, preferably 20 μm or more. When the particle size distribution of the aluminum alloy powder is 100 μm or less and the average particle size of the boron compound particles is 10 μm or less, the boron compound particles are uniformly dispersed, and the dilute portions of the boron compound particles are very small, and the characteristics are stable. There is an effect in making. The average particle size of the aluminum alloy powder is such that cracks are likely to occur during plastic processing such as extrusion or rolling if the difference in the average particle size of particles such as B 4 C described later is large. It is preferable to make it small. If the average particle size becomes too large, the average particle size cannot be increased, for example, uniform mixing with B 4 C particles becomes difficult. On the other hand, if the average particle size is too small, aggregation is likely to occur between fine aluminum alloy powders, This is because uniform mixing with B 4 C particles or the like becomes very difficult. Further, by setting the average particle size within such a range, it is possible to obtain further excellent processability, moldability, and mechanical properties.
In addition, the average particle diameter in this invention shows the value by the laser diffraction type particle size distribution measuring method. The powder shape is not limited, and may be any shape such as a teardrop shape, a true spherical shape, a spheroid shape, a flake shape, or an indefinite shape.
上記アルミニウム合金粉末の製造方法は限定されず、公知の金属粉末の製造方法に従って製造することができる。その製造方法は例えば、アトマイズ法、メルトスピニング法、回転円盤法、回転電極法、その他の急冷凝固法等が挙げられるが、工業的生産にはアトマイズ法、特に溶湯をアトマイズすることにより粉末を製造するガスアトマイズ法が好ましい。
なお、アトマイズ法においては、上記溶湯を通常７００〜１２００℃に加熱してアトマイズすることが好ましい。この温度範囲に設定することにより、より効果的なアトマイズを実施することができるからである。またアトマイズ時の噴霧媒・雰囲気は、空気、窒素、アルゴン、ヘリウム、二酸化炭素、水等あるいはそれらの混合であってもよいが、噴霧媒は、経済的観点から、空気、窒素ガス又はアルゴンガスによるのが好ましい。
The manufacturing method of the said aluminum alloy powder is not limited, It can manufacture according to the manufacturing method of a well-known metal powder. The production method includes, for example, the atomizing method, melt spinning method, rotating disk method, rotating electrode method, and other rapid solidification methods. For industrial production, the atomizing method, in particular, powder is produced by atomizing molten metal. The gas atomizing method is preferred.
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 mixture thereof, but the atomizing medium is air, nitrogen gas or argon gas from an economic viewpoint. Is preferred.
［ホウ素系化合物］
ホウ素系化合物の平均粒径は任意であるが、アルミニウム合金の平均粒径に対して説明したように、これら二種の粉末間の粒径差が少ない方が好ましい。具体的には、Ｂ４Ｃの場合は、１〜２０μｍが好ましい。平均粒径が２０μｍ（好ましくは１０μｍ以下）より大きいと、切断時に鋸歯が直ぐに摩耗してしまう問題があり、また、平均粒径が１μｍ（好ましくは５μｍ以上）より小さいと、これら微細粉末同士で凝集が起こり易くなり、アルミニウム粉末との均一混合が非常に困難になるからである。
なお、本発明の平均粒径は、レーザー回折式粒度分布測定法による値を示す。粉末形状も限定されず、例えば、涙滴状、真級状、回転楕円体状、フレーク状、不定形状等のいずれであってもよい。
[Boron compounds]
The average particle size of the boron-based compound is arbitrary, but as described with respect to the average particle size of the aluminum alloy, it is preferable that the particle size difference between these two kinds of powders is small. Specifically, in the case of B 4 C, 1 to 20 μm is preferable. When the average particle size is larger than 20 μm (preferably 10 μm or less), there is a problem that the saw blade is worn out immediately when cutting, and when the average particle size is smaller than 1 μm (preferably 5 μm or more), these fine powders This is because agglomeration easily occurs and uniform mixing with the aluminum powder becomes very difficult.
In addition, the average particle diameter of this invention shows the value by the laser diffraction type particle size distribution measuring method. The powder shape is not limited, and may be any one of teardrop shape, true grade shape, spheroid shape, flake shape, indefinite shape, and the like.
（２）各工程の説明
（ａ）アルミニウム合金粉末とホウ素系化合物粉末の混合粉末の製造工程
アルミニウム合金粉末と、Ｂ４Ｃ等のホウ素系化合物粉末を用意し、これら粉末を均一に混合する。混合の方法は、公知の方法でよく、例えばＶブレンダー、クロスロータリーミキサー等の各種ミキサー、振動ミル、遊星ミル等を使用し、所定の時間（例えば１０分〜６時間程度）混合すればよい。また、混合は、乾式又は湿式の何れであってもよい。また、混合の際に解砕の目的で、アルミナボール等のメディアを適宜加えてもよい。
(2) Explanation of each step (a) Production process of mixed powder of aluminum alloy powder and boron compound powder Aluminum alloy powder and boron compound powder such as B 4 C are prepared, and these powders are mixed uniformly. The mixing method 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 may be used and mixed for a predetermined time (for example, about 10 minutes to 6 hours). Further, the mixing may be either dry or wet. Moreover, you may add media, such as an alumina ball | bowl, suitably for the purpose of crushing in the case of mixing.
（ｂ）加圧成形工程
Ｂ４Ｃ等のホウ素系化合物粉末とアルミニウム合金の混合粉末を、加圧焼結を行いやすい形状に加圧成形する。仮成形する方法は、公知の方法で良く、例えば冷間静水圧成形、冷間一軸成形やホットプレス成形を用いて、加圧成形すれば良い。
(B) Pressure forming step A mixed powder of boron-based compound powder such as B 4 C and an aluminum alloy is pressure-molded into a shape that facilitates pressure sintering. A known method may be used for the temporary molding, and for example, cold isostatic pressing, cold uniaxial molding, or hot press molding may be used for pressure molding.
（ｃ）脱ガス処理工程
加圧成形体は、減圧雰囲気、不活性ガス雰囲気又は還元雰囲気において、３００〜５７０℃の温度範囲に加熱保持され、脱ガスされる。この工程により、加圧成形体に付着していた水分が気化し除去される。また成形体内部に残っていた気体も除去される。水分や気体を除去させるためには、３００〜５７０℃の温度範囲に４時間以上保持することが好ましい。加熱保持温度が３００℃未満だと水分や気体の除去が、不十分となり、この後の加圧焼結や、熱処理の際に、フクレとなり、欠陥の原因となる。加熱保持温度が５７０℃以上になると、一部焼結が進行し、この後のハンドリングが容易となる。また、誘電加熱が容易となり、加圧焼結の際の加熱が容易となるので４５０℃以上で加熱保持することが好ましい（更に、好ましくは５００℃以上）。十分に仮焼結させるためには、１時間以上保持することが好ましい。加熱保持温度が５７０℃を超えるとアルミニウム合金の溶融や結晶粒の粗大化がおこる虞があるので、加熱保持温度は５７０℃以下にすることが好ましい（更に好ましくは５５０℃以下）。脱ガス後は、常温まで冷却される。なお、３００℃以下まで冷却されるまでは、減圧雰囲気、不活性ガス雰囲気又は還元雰囲気にしておくことが好ましい。更に好ましくは常温まで冷却される。また脱ガス後、そのまま熱間加工温度まで、冷却あるいは加熱し、熱間加工を行っても良い。
(C) Degassing treatment step The pressure-molded body is heated and held in a temperature range of 300 to 570 ° C in a reduced pressure atmosphere, an inert gas atmosphere or a reducing atmosphere, and degassed. By this step, the water adhering to the pressure molded body is vaporized and removed. Further, the gas remaining inside the molded body is also removed. In order to remove moisture and gas, it is preferable to hold in a temperature range of 300 to 570 ° C. for 4 hours or more. If the heating and holding temperature is less than 300 ° C., the removal of moisture and gas becomes insufficient, resulting in blistering in the subsequent pressure sintering and heat treatment, causing defects. When the heating and holding temperature is 570 ° C. or higher, part of the sintering proceeds, and subsequent handling becomes easy. Moreover, since dielectric heating becomes easy and heating at the time of pressure sintering becomes easy, it is preferable to heat and hold at 450 ° C. or higher (more preferably 500 ° C. or higher). In order to sufficiently pre-sinter, it is preferable to hold for 1 hour or more. If the heating and holding temperature exceeds 570 ° C., the aluminum alloy may be melted or the crystal grains may be coarsened. Therefore, the heating and holding temperature is preferably 570 ° C. or less (more preferably 550 ° C. or less). After degassing, it is cooled to room temperature. Note that a reduced pressure atmosphere, an inert gas atmosphere, or a reducing atmosphere is preferably used until cooling to 300 ° C. or lower. More preferably, it is cooled to room temperature. Further, after degassing, the hot working may be performed by cooling or heating to the hot working temperature as it is.
（ｄ）熱間塑性加工（加圧焼結）工程
脱ガス処理を行った仮成形体を所定の温度（好ましくは４００〜５５０℃）に加熱して、押出、鍛造、圧延等の熱間塑性加工を行い、加圧焼結させる。加熱温度が４００℃以下だと変形抵抗値が大きく、熱間加工に大きな力が必要となる。５５０℃を超えると一部溶融や結晶粒の粗大化がおこる虞がある。目的とする形状にするために熱間塑性加工は複数回行っても良いし、また熱間塑性加工の後冷間塑性加工（圧延、鍛造、引き抜き加工等）を行っても良い。冷間塑性加工する場合には、３５０〜４５０℃で加工の前に焼鈍を行うことが好ましい。熱間塑性加工又は冷間塑性加工後、複合材はそのまま使用してもよいし、溶体化処理や人工時効等の熱処理を行っても良い。
(D) Hot plastic working (pressure sintering) step The degassed temporary molded body is heated to a predetermined temperature (preferably 400 to 550 ° C.) to perform hot plasticity such as extrusion, forging, and rolling. Process and pressure sinter. When the heating temperature is 400 ° C. or less, the deformation resistance value is large, and a large force is required for hot working. If it exceeds 550 ° C., there is a risk of partial melting and coarsening of crystal grains. In order to obtain a target shape, the hot plastic working may be performed a plurality of times, or after the hot plastic working, cold plastic working (rolling, forging, drawing, etc.) may be performed. In the case of cold plastic working, it is preferable to perform annealing at 350 to 450 ° C. before working. After hot plastic working or cold plastic working, the composite material may be used as it is, or heat treatment such as solution treatment or artificial aging may be performed.
［本発明の第二の製造方法］
本発明の製造方法の第二の実施形態は、（ａ）上述の組成を有する母材となるアルミニウム合金粉末と、ホウ素系化合物粉末を混合して混合粉末を生成する工程と、（ｂ’）上記混合粉末をアルミニウム製の容器に封入する工程と、（ｃ）加圧成形した成形体を所定雰囲気中で加熱し、脱ガス処理を行う工程と、（ｄ）最後に熱間塑性加工を行う工程とを具備する。
複合材でないアルミニウム容器に封入して熱間塑性加工することにより、複合材表面がアルミニウムに覆われることになり、複合材の耐食性、熱伝導性等が向上する。また塑性加工の際に押出ダイス等の塑性加工工具とホウ素化合物が直接接触しないので、加工工具の寿命が延び、更に複合材表面に表面欠陥も発生しにくくなる。
[Second production method of the present invention]
In the second embodiment of the production method of the present invention, (a) a step of producing a mixed powder by mixing an aluminum alloy powder serving as a base material having the above-described composition and a boron-based compound powder, and (b ′) A step of enclosing the mixed powder in an aluminum container, (c) a step of heating the molded body under pressure molding in a predetermined atmosphere and performing a degassing process, and (d) finally performing a hot plastic working. A process.
By enclosing in an aluminum container that is not a composite material and performing hot plastic working, the surface of the composite material is covered with aluminum, and the corrosion resistance, thermal conductivity, and the like of the composite material are improved. Further, since the plastic working tool such as an extrusion die and the boron compound are not in direct contact with each other during plastic working, the life of the working tool is extended, and surface defects are less likely to occur on the surface of the composite material.
（１）原材料の説明
第一の製造方法に用いられるものと同様の原材料の他、アルミニウム製の容器が準備される。このアルミニウム製容器は、複合体の熱間塑性加工工程後には複合材の表層部に残ることになるが、これを剥がさないで複合体の表層部としたままにできるし、これを剥がしてもよい。但し、剥がされないでそのまま複合体の表層部とされる場合には、複合体に要求される特性に合致したアルミニウムが利用される必要がある。その場合のアルミニウムは純アルミニウム又はアルミニウム合金であるが、簡便には、ＪＩＳ１０７０等の純アルミニウムやＡｌ−Ｃｕ系合金（ＪＩＳ２０１７等）、Ａｌ−Ｍｇ系合金（ＪＩＳ５０５２等）、Ａｌ−Ｍｇ−Ｓｉ系合金（ＪＩＳ６０６１等）、Ａｌ−Ｚｎ−Ｍｇ系合金（ＪＩＳ７０７５等）、Ａｌ−Ｍｎ系合金等の通常のアルミニウム合金を使用することができ、所望される特性、コスト等々を考慮して決定される。
アルミニウム製容器は、缶（本体部）と蓋の形態に予め成形されたものを準備するか、常法により適宜製作する。缶の肉厚は１〜１０ｍｍ程度、好ましくは４〜６ｍｍ程度で、搬送に耐える強度を持たせることが望ましい。蓋は、缶と同材質でも異材質でもよく、後の成形時のガス抜き小孔を少なくとも一以上備えたものとすることができる。
(1) Description of raw materials In addition to the same raw materials as those used in the first manufacturing method, an aluminum container is prepared. This aluminum container will remain on the surface layer of the composite after the hot plastic working step of the composite, but it can be left as the surface of the composite without peeling it off. Good. However, when it is used as it is as the surface layer portion of the composite without being peeled off, it is necessary to use aluminum that matches the properties required for the composite. In this case, the aluminum is pure aluminum or an aluminum alloy. For simplicity, pure aluminum such as JIS1070, Al—Cu alloy (JIS2017, etc.), Al—Mg alloy (JIS5052 etc.), Al—Mg—Si Ordinary aluminum alloys such as alloys (JIS6061 etc.), Al-Zn-Mg alloys (JIS7075 etc.), Al-Mn alloys can be used, and are determined in consideration of desired characteristics, cost, etc. .
The aluminum container is prepared in advance in the form of a can (main body part) and a lid, or is appropriately manufactured by a conventional method. The thickness of the can is about 1 to 10 mm, preferably about 4 to 6 mm, and it is desirable that the can be strong enough to withstand conveyance. The lid may be the same material as the can or a different material, and may be provided with at least one small vent hole for subsequent molding.
（２）各工程の説明
（ａ）アルミニウム合金粉末とホウ素系化合物粉末の混合粉末の製造工程
第一の製造方法の場合と同様にして、アルミニウム合金粉末とホウ素系化合物粉末を常法により均一に混合する。
(2) Explanation of each process (a) Manufacturing process of mixed powder of aluminum alloy powder and boron-based compound powder In the same manner as in the first manufacturing method, the aluminum alloy powder and boron-based compound powder are uniformly made by a conventional method. Mix.
（ｂ’）容器封入工程
工程（ａ）で得られた混合粉末を、前述のアルミニウム製容器の本体部に充填する。ついで、振動を加えるなどして粉末周囲のガス抜きを行った後、蓋部を溶接等によって取り付け、搬送時に粉末が漏れ出ないようにして容器封入体を製造する。
尚、混合粉末を容器に封入する前に、加圧成形しておいてもよく、この場合は、第一の製造方法の加圧成形工程に容器封入工程が追加的に施されることになる。
(B ′) Container Enclosing Step The mixed powder obtained in the step (a) is filled in the main body of the aforementioned aluminum container. Next, after degassing around the powder by applying vibration or the like, the lid is attached by welding or the like, and the container enclosure is manufactured so that the powder does not leak during transportation.
In addition, before encapsulating the mixed powder in the container, it may be subjected to pressure molding. In this case, the container encapsulation process is additionally performed in the pressure molding process of the first manufacturing method. .
（ｃ）脱ガス処理工程
工程（ｂ’）で得られた容器封入体を、第一の製造方法と同様にして脱ガス処理する。すなわち、減圧雰囲気、不活性ガス雰囲気又は還元雰囲気において、２００℃以上、好ましくは４５０℃以上、より好ましくは５００℃以上で、６００℃以下、好ましくは５５０℃以下の温度範囲に加熱保持し、脱ガス処理した後、好ましくは２００℃以下まで冷却されるまでは、減圧雰囲気、不活性ガス雰囲気又は還元雰囲気にて、常温まで冷却するか、あるいはそのまま熱間加工温度まで、冷却あるいは加熱する。
(C) Degassing treatment step The container enclosure obtained in the step (b ') is degassed in the same manner as in the first production method. That is, in a reduced pressure atmosphere, an inert gas atmosphere or a reducing atmosphere, it is heated and held in a temperature range of 200 ° C. or higher, preferably 450 ° C. or higher, more preferably 500 ° C. or higher, 600 ° C. or lower, preferably 550 ° C. or lower. After the gas treatment, until it is cooled to preferably 200 ° C. or lower, it is cooled to room temperature in a reduced pressure atmosphere, an inert gas atmosphere or a reducing atmosphere, or cooled or heated to the hot working temperature as it is.
（ｄ）熱間塑性加工（加圧焼結）工程
工程（ｃ）で得られた仮成形体を、第一の製造方法と同様にして、所定の温度（好ましくは４００〜５５０℃）に加熱して、押出、鍛造、圧延等の熱間塑性加工を一又は複数回行い、また場合によっては更に冷間塑性加工（圧延、鍛造、引き抜き加工等）を行って、所望の形状に加工する。
このようにして形成された複合材の表面にはアルミニウム製容器が残り、アルミニウム表層部でクラッドされた成形体が得られるが、前述のように、このクラッドされたアルミニウム製容器は、剥がしても剥がさなくても良い。
(D) Hot plastic working (pressure sintering) step The temporary molded body obtained in step (c) is heated to a predetermined temperature (preferably 400 to 550 ° C) in the same manner as in the first production method. Then, hot plastic working such as extrusion, forging, and rolling is performed one or more times, and in some cases, cold plastic working (rolling, forging, drawing, etc.) is performed to obtain a desired shape.
An aluminum container remains on the surface of the composite material thus formed, and a molded body clad with the aluminum surface layer portion is obtained. As described above, this clad aluminum container is peeled off. It does not have to be peeled off.
以下、本発明を、実施例を参照しながら詳細に説明する。
［実施例１］
ガスアトマイズ法で製造した表１の組成の平均粒径３０μｍのアルミニウム合金粉末に、平均粒径１０μｍのＢ４Ｃ粉末を、５質量％の割合となるようにＶブレンダー混合機を用いて混合し、冷間静水圧成形で、２００ｍｍ直径の円筒状に加圧成形した。得られた加圧成形体を、減圧炉で５６０℃×４時間保持し、脱ガスを行った後、減圧雰囲気中で常温まで冷却した。その後再度４８０℃まで加熱し、熱間押出加工を行い、１００ｍｍ幅×５ｍｍ厚さの平板に塑性加工した。
得られた押出材について、高温強度、耐熱性及び耐食性を試験した。
ここで、高温強度は、２００℃での引張破断強度試験を行い、１１０Ｍｐａ以上の引張破断強度を示したものを合格品とした。耐熱性は、２００℃で１００時間加熱後に、２００℃での引張破断強度試験を行い、１００Ｍｐａ以上の引張破断強度を示したものを合格品とした。また、耐食性は、室温で食塩水中に５００時間浸漬した場合の純アルミニウムの減量を１（１０ｍｇ／ｄｍ２以下）として比較することにより評価した。この判定基準では６０６１−Ｔ６材は４となるので、合格品は４以下とした。
上記の試験結果を表２に示す。
また比較例として、ＪＩＳ規格の１０５０アルミニウム合金、２０１７アルミニウム合金、３００３アルミニウム合金、５０５２アルミニウム合金、６０６１アルミニウム合金（詳細な組成はそれぞれ表１に記載）のアルミニウム合金を母材とする複合材の押出材を同様の方法で製造し、同様の試験方法で高温強度、耐熱性及び耐食性を試験した。その結果も表２に併せて示す。尚、試験材は全てＴ１材（押し出しのまま）である。
Hereinafter, the present invention will be described in detail with reference to examples.
[Example 1]
A B 4 C powder having an average particle size of 10 μm was mixed with an aluminum alloy powder having an average particle size of 30 μm having the composition shown in Table 1 manufactured by the gas atomization method using a V blender mixer so as to have a ratio of 5 mass%. By cold isostatic pressing, it was pressure molded into a 200 mm diameter cylinder. The obtained press-molded body was held at 560 ° C. for 4 hours in a vacuum furnace, degassed, and then cooled to room temperature in a vacuum atmosphere. Then, it was heated again to 480 ° C., subjected to hot extrusion, and plastic processed into a flat plate having a width of 100 mm × 5 mm.
About the obtained extrusion material, high temperature strength, heat resistance, and corrosion resistance were tested.
Here, the high temperature strength was subjected to a tensile breaking strength test at 200 ° C., and the one showing a tensile breaking strength of 110 Mpa or more was regarded as an acceptable product. As for heat resistance, after heating at 200 ° C. for 100 hours, a tensile breaking strength test at 200 ° C. was performed, and a product exhibiting a tensile breaking strength of 100 Mpa or more was regarded as an acceptable product. Corrosion resistance was evaluated by comparing the weight loss of pure aluminum as 1 (10 mg / dm2 or less) when immersed in saline at room temperature for 500 hours. In this criterion, 6061-T6 material is 4, so the number of acceptable products is 4 or less.
The test results are shown in Table 2.
As a comparative example, extrusion of a composite material based on a JIS standard 1050 aluminum alloy, 2017 aluminum alloy, 3003 aluminum alloy, 5052 aluminum alloy, and 6061 aluminum alloy (detailed compositions are listed in Table 1). The material was manufactured by the same method, and the high temperature strength, heat resistance and corrosion resistance were tested by the same test method. The results are also shown in Table 2. All the test materials are T1 materials (as extruded).
表２より、本発明例である合金番号１〜１０は、本材料の主要用途における高温強度、耐熱性、耐食性及び押出性（押出時の圧力と押出材表面状態で評価）などの評価では要求仕様を満足していることが分かる。主要添加元素のＭｎ、Ｍｇ、Ｆｅ、Ｃｕを所定の量的範囲で、そして更にはＳｉを所定の範囲で添加することによって十分な性能が得られるが、それらの範囲を下回る合金、上回る合金は、高温強度、耐熱性は十分であるが、耐食性、製造可否（生産性）では不満足なものとなり、実用化を困難にしている。
すなわち、ＪＩＳ３００３、５０５２、６０６１は耐熱性で不合格であり、この欠点を改良するには、各元素の作用効果の欄で記述したように、Ｍｎ、Ｍｇ、Ｆｅ、Ｃｕの適量を選択する必要があった。Ｍｎが０．８％未満では、Ｍｇを０．２％、Ｆｃ、Ｃｕをそれぞれ０．１％添加しても耐熱性への効果が減少した。これは、母材中に存在するＭｎ化合物量が少なくなり、高温時の変形を防止する微細化合物の役割が減じたためと思われる。また、Ｍｇが少ない場合も耐熱性は低下し、高温でのＭｇの固溶強化が小さくなったためと考えられる。Ｆｅ量の少ない場合は、Ａｌ−Ｆｅ−Ｍｎ（−Ｓｉ）系化合物量の減少、そしてＣｕ量の少ない場合は、高温での微細化合物の析出促進効果が小さくなったためと考えられる。
ＪＩＳ規格品について見れば、ＪＩＳ３００３は強度不足である。ＪＩＳ５０５２及びＪＩＳ６０６１は耐熱性の低下が大きい。これらは、上記の化合物の生成量が少なく、微細化合物の高温での成長を抑制できなかったためである。
From Table 2, Alloy Nos. 1 to 10, which are examples of the present invention, are required for evaluations such as high-temperature strength, heat resistance, corrosion resistance, and extrudability (evaluated by the pressure during extrusion and the surface condition of the extruded material) in the main applications of the material. It can be seen that the specification is satisfied. Sufficient performance can be obtained by adding the main additive elements Mn, Mg, Fe, Cu in a predetermined quantitative range, and further Si in a predetermined range. However, the high-temperature strength and heat resistance are sufficient, but the corrosion resistance and manufacturability (productivity) are unsatisfactory, making it difficult to put to practical use.
That is, JIS3003, 5052, and 6061 are heat resistant and rejected, and in order to improve this defect, it is necessary to select appropriate amounts of Mn, Mg, Fe, and Cu as described in the column of the effect of each element. was there. When Mn was less than 0.8%, the effect on heat resistance decreased even when 0.2% Mg, 0.1% Fc and Cu were added. This is probably because the amount of the Mn compound present in the base material is reduced, and the role of the fine compound for preventing deformation at high temperature is reduced. Further, it is considered that the heat resistance is lowered when Mg is small, and the solid solution strengthening of Mg at high temperature is reduced. It is considered that when the amount of Fe is small, the amount of Al—Fe—Mn (—Si) compound is decreased, and when the amount of Cu is small, the effect of promoting the precipitation of fine compounds at high temperatures is reduced.
Looking at JIS standard products, JIS 3003 is insufficient in strength. JIS5052 and JIS6061 have a large reduction in heat resistance. These are because the amount of the compound produced is small and the growth of the fine compound at a high temperature could not be suppressed.
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