JP2008248297A - Rolled aluminum alloy sheet with excellent thermal conductivity, strength and bendability, and its manufacturing method - Google Patents

Rolled aluminum alloy sheet with excellent thermal conductivity, strength and bendability, and its manufacturing method Download PDF

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JP2008248297A
JP2008248297A JP2007089967A JP2007089967A JP2008248297A JP 2008248297 A JP2008248297 A JP 2008248297A JP 2007089967 A JP2007089967 A JP 2007089967A JP 2007089967 A JP2007089967 A JP 2007089967A JP 2008248297 A JP2008248297 A JP 2008248297A
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strength
aluminum alloy
thermal conductivity
rolling
conductivity
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JP4933326B2 (en
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Sotaro Sekida
関田宗太郎
Katsumi Koyama
小山克己
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Furukawa Sky Kk
古河スカイ株式会社
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Abstract

<P>PROBLEM TO BE SOLVED: To obtain a rolled sheet having thermal conductivity, strength and bendability, all required of a material for a heat dissipating component, by a low-cost manufacturing method. <P>SOLUTION: An ingot of an aluminum alloy, having a composition which consists of 1.1 to 1.5% Si, 0.3 to 0.6% Mg, 0.6 to 0.8% Cu, further 0.005 to 0.15% Ti independently or in combination with 0.0001 to 0.05% B, and the balance Al with inevitable impurities and in which Fe as an impurity is limited to ≤0.35%, is used. The aluminum-alloy ingot is subjected to homogenizing treatment at 500 to 570°C for 1 to 24 hr. Subsequently, hot rolling is started at ≥450°C and finished at ≤300°C. Further, cold rolling is applied at ≥60% rolling rate, and the resulting cold rolled aluminum-alloy sheet is subjected to final annealing at 140 to 200°C. <P>COPYRIGHT: (C)2009,JPO&INPIT

Description

この発明は、プラズマディスプレーなどの電子映像部品、パソコンなどの電子部品、家庭用電化製品部品などの放熱板・筐体・プリント基板などに使用される放熱部品用アルミニウム合金圧延板に関するものであり、特に熱伝導性と強度と曲げ加工性に優れたAl-Si-Mg系のアルミニウム合金圧延板およびその低コストな製造方法に関するものである。   This invention relates to an aluminum alloy rolled plate for heat dissipation parts used for heat sinks, housings, printed boards, etc., such as electronic video parts such as plasma displays, electronic parts such as personal computers, household electrical appliance parts, In particular, the present invention relates to an Al—Si—Mg-based aluminum alloy rolled plate excellent in thermal conductivity, strength, and bending workability, and a low-cost manufacturing method thereof.
特に、プラズマディスプレーは映像部分と電子部品が集積した部分とで構成されていて、薄く壁に掛けられる構造になっているため、映像部分と電子部品は接近した構造となっている。その映像部分は発光素子の集合体であり、素子には高電圧が負荷されるため発熱量が多く、周囲への影響は避けられない。     In particular, the plasma display is composed of an image portion and a portion where electronic parts are integrated, and is thinly hung on a wall, so that the image portion and the electronic parts are close to each other. The image portion is an aggregate of light emitting elements, and since a high voltage is applied to the elements, a large amount of heat is generated, and the influence on the surroundings is inevitable.
プラズマディスプレーの発熱により、電気回路として機能する構造物が温度上昇してノイズの原因となったり、使用している半導体電子部品が不具合を起こして故障原因となりかねない。   Due to the heat generated by the plasma display, the structure that functions as an electric circuit rises in temperature and may cause noise, or the semiconductor electronic component that is used may malfunction and cause failure.
このため映像部分の発熱から高機能を誇る電子部品を保護する目的で、両者の間に放熱部品を置いて、映像部分の発熱を分散させる放熱機構を設けている。
この放熱部品として求められる特性としては、高導電率で高強度、かつ曲げ加工性が良好な、厚さ1mm前後の板材である。
For this reason, for the purpose of protecting electronic components boasting high functionality from heat generation in the video portion, a heat dissipation mechanism is provided to disperse heat generation in the video portion by placing a heat dissipation component between them.
As a characteristic required for the heat dissipation component, a plate material having a thickness of about 1 mm and having high conductivity, high strength, and good bending workability.
なお、導電率と熱伝導度の関係は、後述の特許文献2(特開2005−264174号公報)の図1に示される如く高い相関があり、導電率の高い材料ほど熱伝導度も高い材料であると言える。   The relationship between electrical conductivity and thermal conductivity has a high correlation as shown in FIG. 1 of Patent Document 2 (Japanese Patent Laid-Open No. 2005-264174) described later, and a material with higher electrical conductivity has a higher electrical conductivity. It can be said that.
熱伝導性の優れたAl-Si-Mg系合金板の製造方法を開示したものとして、例えば特許文献1が挙げられる。
特許第3495263号公報
For example, Patent Document 1 is disclosed as a method for manufacturing an Al—Si—Mg-based alloy plate having excellent thermal conductivity.
Japanese Patent No. 3495263
しかしながら、特許文献1記載の発明は、優れた熱伝導性とJIS5052合金並みの高強度は得られるものの、熱間粗圧延時の任意パス工程での制約(パス前の材料温度350〜440℃、パス間の冷却速度50℃/min以上、パス上り材料温度250〜340℃、上り板厚10mm以下)が厳しく、これを達成するには多大な設備投資が必要となり、却って高コストとなってしまう。   However, although the invention described in Patent Document 1 provides excellent thermal conductivity and high strength similar to JIS 5052 alloy, restrictions in the optional pass process during hot rough rolling (material temperature 350 to 440 ° C before pass, The cooling rate between passes is 50 ° C./min or more, the pass rising material temperature is 250 to 340 ° C., and the rising plate thickness is 10 mm or less). To achieve this, a large capital investment is required, and the cost is increased. .
また、熱伝導性の優れたAl-Si-Mg系合金板および製造方法を開示したものとして、例えば特許文献2が挙げられる。
特開2005−264174号公報
Patent Document 2 is an example of an Al—Si—Mg-based alloy plate having excellent thermal conductivity and a manufacturing method disclosed therein.
JP 2005-264174 A
しかしながら、特許文献2(特開2005−264174号公報)の発明は、そこそこの熱伝導性と強度と成形加工性は優れているものの、製造工程の中の冷間圧延途中で溶体化処理(500〜570℃、冷却速度1.0℃/sec以上)を行うことが必須のため、これまた高コストとなってしまう。   However, although the invention of patent document 2 (Unexamined-Japanese-Patent No. 2005-264174) is excellent in moderate heat conductivity, intensity | strength, and moldability, it is a solution treatment (500 in the middle of the cold rolling in a manufacturing process). ˜570 ° C., cooling rate of 1.0 ° C./sec or more) is essential, which also increases the cost.
前述のように、放熱部品に加工して使用される熱伝導性の優れたAl-Si-Mg系合金板の製造工程において、設備投資や溶体化処理が不要であるなどによる低コスト化が求められている。   As mentioned above, in the manufacturing process of Al-Si-Mg alloy plates with excellent thermal conductivity that are processed into heat-dissipating parts, cost reduction is required due to the absence of equipment investment and solution treatment. It has been.
この発明は以上の事情を背景としてなされたもので、放熱部品としての特性は損なわずに低コストで製造可能なアルミニウム合金圧延板およびその製造方法を提供することを目的とするものである。   The present invention has been made against the background described above, and it is an object of the present invention to provide an aluminum alloy rolled sheet that can be manufactured at low cost without impairing the characteristics as a heat dissipation component and a method for manufacturing the aluminum alloy rolled sheet.
前述のような課題を解決するため、本発明者らは鋭意実験・検討を重ねた結果、適切な成分と、適切なプロセス条件を適用することによって、放熱部品用のアルミニウム合金圧延板としての課題を解決できることを見い出し、この発明をなすに至ったのである。   In order to solve the above-mentioned problems, the present inventors have conducted intensive experiments and examinations, and as a result, by applying appropriate components and appropriate process conditions, problems as an aluminum alloy rolled plate for heat dissipation parts As a result, the present inventors have found that the present invention can be solved.
具体的には請求項1の発明の熱伝導性と強度と曲げ加工性に優れたアルミニウム合金圧延板は、Si1.1〜1.5%、Mg0.3〜0.6%、Cu0.6〜0.8%を含有し、さらにTi0.005〜0.15%を単独であるいはB0.0001〜0.05%と共に含有し、不純物としてのFeを0.35%以下に規制し、残部がAlおよび不可避的不純物よりなり、かつ導電率が55%IACS以上、引張強さが215N/mm以上であることを特徴とする。 Specifically, the aluminum alloy rolled sheet excellent in thermal conductivity, strength and bending workability of the invention of claim 1 is Si 1.1 to 1.5%, Mg 0.3 to 0.6%, Cu 0.6 to Containing 0.8%, further containing Ti 0.005 to 0.15% alone or together with B0.0001 to 0.05%, restricting Fe as an impurity to 0.35% or less, the balance being Al And an inevitable impurity, having a conductivity of 55% IACS or more and a tensile strength of 215 N / mm 2 or more.
そして、請求項2の発明は、請求項1記載の化学組成を有するアルミニウム合金の鋳塊に、500〜570℃の範囲内の温度で1〜24時間の均質化処理を施し、次いで熱間圧延を450℃以上の温度で開始し300℃以下で終了し、さらに60%以上の圧延率で冷間圧延を施した後、140〜200℃の最終焼鈍を施し、これにより最終焼鈍板の導電率が55%IACS以上、引張強さが215N/mm以上とすることを特徴とする熱伝導性と強度と曲げ加工性に優れたアルミニウム合金圧延板の製造方法である。 In the invention of claim 2, the ingot of the aluminum alloy having the chemical composition of claim 1 is subjected to a homogenization treatment for 1 to 24 hours at a temperature in the range of 500 to 570 ° C., and then hot rolled. Is started at a temperature of 450 ° C. or higher and finished at 300 ° C. or lower. Further, after cold rolling at a rolling rate of 60% or higher, a final annealing of 140 to 200 ° C. is performed, whereby the conductivity of the final annealed plate Is a method for producing an aluminum alloy rolled sheet excellent in thermal conductivity, strength and bending workability, characterized in that the tensile strength is 215 N / mm 2 or more.
本発明によれば、Al−Si−Mg系合金を用い、適切なプロセス条件を適用することにより、熱伝導性と強度と曲げ加工性は損なわずに製造コストが低減できるアルミニウム合金圧延板を製造することができる。   According to the present invention, by using an Al—Si—Mg based alloy and applying appropriate process conditions, an aluminum alloy rolled sheet that can reduce the manufacturing cost without impairing thermal conductivity, strength, and bending workability is manufactured. can do.
先ずこの発明における成分組成の限定理由について説明する。   First, the reasons for limiting the component composition in the present invention will be described.
Si:SiとMgはこの合金の強度、曲げ加工性、導電率などの特性を確保するために必要な元素である。Si量はMg量とのバランスで放熱部品の強度を確保するが1.5%を超えると導電率の低下や曲げ加工性を阻害する要因となる。一方、Si量が1.1%未満であると強度不足の原因となる。そこでSi量は1.1〜1.5%の範囲とする。 Si: Si and Mg are elements necessary for securing properties such as strength, bending workability and conductivity of the alloy. The amount of Si secures the strength of the heat dissipation component in balance with the amount of Mg, but if it exceeds 1.5%, it becomes a factor that hinders the decrease in conductivity and bending workability. On the other hand, if the Si content is less than 1.1%, the strength is insufficient. Therefore, the Si amount is in the range of 1.1 to 1.5%.
Mg:Mgは強度を向上させ、放熱部品の強度を確保するために必要な元素であり、0.3%未満だと強度不足となり、0.6%を超えると導電率低下の要因となる。そこでMg量は0.3〜0.6%の範囲とする。 Mg: Mg is an element necessary for improving the strength and securing the strength of the heat dissipation component. If it is less than 0.3%, the strength is insufficient, and if it exceeds 0.6%, it causes a decrease in conductivity. Therefore, the Mg amount is set in the range of 0.3 to 0.6%.
Cu:Cuも強度を確保するために必要な元素であり、0.6%未満だと強度不足となり、0.8%を超えると導電率低下の要因となる。そこでCu量は0.6〜0.8%の範囲とする。 Cu: Cu is also an element necessary for ensuring the strength. If it is less than 0.6%, the strength is insufficient, and if it exceeds 0.8%, the conductivity decreases. Therefore, the Cu amount is in the range of 0.6 to 0.8%.
Ti:Tiは鋳塊の結晶粒の微細化に効果があり、鋳塊割れを防止する。0.005%未満だと効果がなく、0.15%を超えると初晶AlTiが晶出して曲げ加工性の劣化や導電率低下の要因となる。そこでTi量は0.005〜0.15%の範囲とする。
また、鋳塊の結晶粒の微細化の効果を強めるために、TiとBを複合添加することも行われている。その場合のB量は1ppm(0.0001%)未満では効果がなく、500ppm(0.05%)を超えるとTiBが生成して曲げ加工性が阻害されるので、B量は1〜500ppmの範囲が望ましい。
従って、結局、Ti0.005〜0.15%を単独であるいはB0.0001〜0.05%と共に含有させる。
Ti: Ti is effective in refining the crystal grains of the ingot and prevents ingot cracking. If it is less than 0.005%, there is no effect, and if it exceeds 0.15%, primary Al 3 Ti is crystallized, which causes a deterioration in bending workability and a decrease in conductivity. Therefore, the Ti amount is in the range of 0.005 to 0.15%.
In addition, in order to enhance the effect of refining the crystal grains of the ingot, Ti and B are added in combination. In that case, if the amount of B is less than 1 ppm (0.0001%), there is no effect, and if it exceeds 500 ppm (0.05%), TiB 2 is generated and bending workability is inhibited, so the amount of B is 1 to 500 ppm. A range of is desirable.
Therefore, eventually, Ti 0.005 to 0.15% is contained alone or together with B0.0001 to 0.05%.
Fe:Feはアルミスクラップやアルミ地金などに含有される不純物元素であり、多すぎるとAl-Fe系金属間化合物のサイズが大きくなって曲げ加工性の劣化や導電率低下の要因となる。そこでFe量は0.35%以下に規制する。 Fe: Fe is an impurity element contained in aluminum scrap, aluminum metal, etc. If it is too much, the size of the Al—Fe-based intermetallic compound becomes large, which causes a deterioration in bending workability and a decrease in conductivity. Therefore, the amount of Fe is restricted to 0.35% or less.
上記以外のMn、Cr、Znなどの不純物元素は各々0.10%以下であれば、本発明のアルミニウム合金圧延板の性能を損なうことはない。   If impurity elements other than the above, such as Mn, Cr, and Zn, are each 0.10% or less, the performance of the aluminum alloy rolled sheet of the present invention will not be impaired.
さらにこの発明では、圧延にて得られた冷間圧延板を焼鈍した最終焼鈍板の特性値を規定しており、これらについて以下に説明する。   Furthermore, in this invention, the characteristic value of the final annealing board which annealed the cold rolled sheet obtained by rolling is prescribed | regulated, and these are demonstrated below.
本発明においては、最終焼鈍板の導電率は55%IACS以上、引張強さは215N/mm以上と規定している。その理由は次の通りである。 In the present invention, the electrical conductivity of the final annealed plate is specified to be 55% IACS or higher, and the tensile strength is specified to be 215 N / mm 2 or higher. The reason is as follows.
すなわち、前述の如く、放熱部品材として問題のないレベルの導電率は50%IACS以上、一方パネル強度は引張強さで200N/mm以上であることから、本発明は両特性のやや高めを狙って導電率は55%IACS以上、引張強さは215N/mm以上を目標とした。 That is, as described above, the conductivity level at which there is no problem as a heat radiating component material is 50% IACS or more, while the panel strength is 200 N / mm 2 or more in terms of tensile strength. Aiming at a conductivity of 55% IACS or more and a tensile strength of 215 N / mm 2 or more.
また、放熱部品用材として多用されているアルミニウム合金圧延板のプレス成形加工は比較的浅い形状のため問題ないが、曲げ加工においては90°曲げで内側曲げ半径1.5mmの厳しい曲げ加工部もあるため、この曲げ条件で割れないことを本発明の目標条件とした。   In addition, there is no problem because the press forming of the aluminum alloy rolled plate, which is often used as a material for heat dissipation parts, has a relatively shallow shape, but there is a severe bending portion with an inner bending radius of 1.5 mm by bending at 90 °. Therefore, the target condition of the present invention is not to break under this bending condition.
次にこの発明の放熱部品用アルミニウム合金圧延板の製造方法について説明する。   Next, the manufacturing method of the aluminum alloy rolled sheet for heat radiating components of this invention is demonstrated.
この発明の放熱部品用アルミニウム合金圧延板の製法上の特徴は、熱間圧延中の任意パス工程での制約を受けずに圧延を施して300℃以下で終了し、製造工程途中の溶体化処理を省略し、冷間圧延を60%以上の比較的大きな圧延率で行うことを規定することにより、目的とする導電率と強度と曲げ加工性を低コストで達成するものである。   The manufacturing feature of the aluminum alloy rolled sheet for heat-radiating parts of the present invention is that it is rolled at 300 ° C. or less without being restricted by the optional pass process during hot rolling, and is a solution treatment during the manufacturing process. By omitting the above and specifying that the cold rolling is performed at a relatively high rolling rate of 60% or more, the desired electrical conductivity, strength, and bending workability can be achieved at a low cost.
先ず前述のようなアルミニウム合金を溶解し、常法に従ってDC鋳造などによって鋳造する。   First, an aluminum alloy as described above is melted and cast by DC casting or the like according to a conventional method.
得られた鋳塊を均質化処理してから熱間圧延を施し、さらに冷間圧延を施して0.5〜2.0mm程度の板厚とし、最後に最終焼鈍を施して製品とする。   The obtained ingot is homogenized and then hot-rolled, further cold-rolled to a thickness of about 0.5 to 2.0 mm, and finally annealed to obtain a product.
ここで、均質化処理は500〜570℃の範囲内の温度で1〜24時間保持の条件とする。均質化処理温度が500℃未満では均質化が不足して曲げ加工性が悪く、一方570℃を越えれば溶解する恐れがある。また保持時間が1時間未満では均質化が不足し、また24時間を越える保持は均質化が飽和して経済的に無駄である。   Here, the homogenization treatment is carried out at a temperature in the range of 500 to 570 ° C. for 1 to 24 hours. If the homogenization temperature is less than 500 ° C., homogenization is insufficient and bending workability is poor, whereas if it exceeds 570 ° C., there is a risk of dissolution. If the holding time is less than 1 hour, homogenization is insufficient, and holding for more than 24 hours is economically wasteful because the homogenization is saturated.
上述のように均質化処理した後、直ちに熱間圧延を開始するが、その熱間圧延開始温度は450℃以上とする。熱間粗圧延開始温度が450℃未満では熱間加工性が悪く、熱間圧延効率が悪い。なお、熱間粗圧延は均質化処理後の鋳塊を一旦室温まで下げてから450℃以上に加熱して開始してもよい。   Although hot rolling is started immediately after homogenization as described above, the hot rolling start temperature is set to 450 ° C. or higher. When the hot rough rolling start temperature is less than 450 ° C., the hot workability is poor and the hot rolling efficiency is poor. The hot rough rolling may be started by once lowering the ingot after homogenization to room temperature and then heating it to 450 ° C. or higher.
また熱間圧延の終了温度は300℃以下とする。熱間圧延終了温度が300℃を越えると部分再結晶や完全再結晶が起こり、最終板の強度低下やバラツキの原因となる。   Moreover, the end temperature of hot rolling shall be 300 degrees C or less. When the hot rolling finish temperature exceeds 300 ° C., partial recrystallization or complete recrystallization occurs, which causes a decrease in strength and variation of the final plate.
熱間圧延後に施す冷間圧延は圧延率が60%以上で行なう。冷間圧延率が60%未満では冷間ひずみが不足して強度不足となる。   Cold rolling performed after hot rolling is performed at a rolling rate of 60% or more. If the cold rolling rate is less than 60%, the cold strain is insufficient and the strength is insufficient.
さらにまた、冷間圧延後に施す最終焼鈍は140〜200℃で行う。140℃未満では伸びが不足して曲げ加工性が劣化し、200℃を超えると強度が低下して強度不足となり好ましくない。なお、軟化を抑えるために180℃以下で最終焼鈍を行うのが好ましい。   Furthermore, the final annealing performed after cold rolling is performed at 140 to 200 ° C. If it is less than 140 ° C., the elongation is insufficient and bending workability is deteriorated, and if it exceeds 200 ° C., the strength is lowered and the strength is insufficient. In addition, in order to suppress softening, it is preferable to perform final annealing at 180 degrees C or less.
表1の合金番号1〜10に示す合金は、常法にて溶解し、それぞれ、DC鋳造法にて厚さ450mm×幅1080mm×長さ2800mmの鋳塊に鋳造した。   The alloys shown in Alloy Nos. 1 to 10 in Table 1 were melted by a conventional method and cast into ingots each having a thickness of 450 mm × width of 1080 mm × length of 2800 mm by a DC casting method.
得られた鋳塊に対し、表2の製造工程番号A〜Hの条件を組み合わせて、表3に示す試料番号1A〜10Aの冷間圧延板(いずれも厚さ1.0mm×幅1000mm×コイル)とした後、バッチ炉焼鈍にて最終焼鈍板とした。   The obtained ingots were combined with the conditions of production process numbers A to H in Table 2, and cold rolled sheets of sample numbers 1A to 10A shown in Table 3 (all thickness 1.0 mm × width 1000 mm × coil Then, the final annealed plate was obtained by batch furnace annealing.
各最終焼鈍板について、導電率は圧延方向に平行に板厚×幅50mm×長さ1000mm(測定基準長さ500mm)の試験片を採取し、ダブルブリッジ法により比抵抗値を測定し、標準銅の比抵抗値を100として導電率を算出した。   For each final annealed plate, the electrical conductivity was taken in parallel with the rolling direction, and a test piece of plate thickness x width 50 mm x length 1000 mm (measurement reference length 500 mm) was taken, the specific resistance value was measured by the double bridge method, and standard copper The electrical conductivity was calculated with a specific resistance value of 100 as 100.
また、強度についてはJISZ2201に定める5号引張試験片にて圧延方向に平行方向の引張強さと伸びを求めた。 Moreover, about the intensity | strength, the tensile strength and elongation of the direction parallel to a rolling direction were calculated | required with the No. 5 tensile test piece prescribed | regulated to JISZ2201.
さらに曲げ加工性については、圧延方向に対し直角方向(曲げ性の劣る方向)に切出したJISZ2204に定める3号曲げ試験片にて90°曲げ試験を実施した。90°曲げ試験は、前述の説明の通りの1.5mmの内側曲げ半径にて行ない、曲げ加工性の評価は10倍のルーペで観察し、割れが発生しなければ合格(○)、割れが発生したものは不合格(×)とした。   Further, regarding the bending workability, a 90 ° bending test was performed with a No. 3 bending test piece defined in JISZ2204 cut out in a direction perpendicular to the rolling direction (a direction inferior in bendability). The 90 ° bending test is performed at an inner bending radius of 1.5 mm as described above, and the evaluation of bending workability is observed with a magnifying glass of 10 times. What was generated was determined to be rejected (x).
それぞれの結果を表3に併せて示す。   The respective results are also shown in Table 3.
表3において、試料番号1A、1B、1C、2Aの最終焼鈍板は、いずれも成分組成および製造工程の両者がこの発明で規定する条件を満たす発明例であり、最終焼鈍板の導電率は55%IACS以上、引張強さはJIS5052−H32下限以上の215N/mm以上の高強度を有し、しかも曲げ加工性に優れた材料であることが明らかである。 In Table 3, the final annealed plates of sample numbers 1A, 1B, 1C, and 2A are all examples of the conditions that both the component composition and the manufacturing process satisfy the conditions defined in the present invention, and the conductivity of the final annealed plate is 55. It is apparent that the material has a high tensile strength of 215 N / mm 2 or more which is higher than the lower limit of JIS5052-H32 and has excellent bending workability.
一方、試料番号1D、1E、1F、1G、1H、の最終焼鈍板は、この発明で規定する成分組成条件を満たした合金であるが、製造工程条件がこの発明で規定する条件から外れた比較例である。   On the other hand, the final annealed plates of sample numbers 1D, 1E, 1F, 1G, and 1H are alloys that satisfy the component composition conditions specified in the present invention, but the manufacturing process conditions are out of the conditions specified in the present invention. It is an example.
1Dは均質化処理温度が低すぎたため均質化が不足して曲げ加工性が劣化してしまった。また、熱間圧延開始温度も低かったため熱間加工性が悪く、熱間圧延に時間がかかってしまった。   In 1D, since the homogenization temperature was too low, homogenization was insufficient and bending workability was deteriorated. Moreover, since the hot rolling start temperature was low, the hot workability was poor and the hot rolling took time.
また1Eは熱間圧延終了温度が高すぎたため熱間圧延終了時に部分再結晶が起こり、引張強さが低下してしまった。   Further, 1E had a hot rolling end temperature that was too high, so that partial recrystallization occurred at the end of hot rolling, resulting in a decrease in tensile strength.
さらに1Fは熱間圧延後の冷間圧延率が不足したため引張強さが低下してしまった。   Furthermore, the tensile strength of 1F decreased because the cold rolling rate after hot rolling was insufficient.
また1Gは最終焼鈍温度が低すぎたため伸びが不足して曲げ加工性が劣化してしまった。   In addition, since 1G had a final annealing temperature too low, elongation was insufficient and bending workability was deteriorated.
さらに1Hは最終焼鈍温度が高すぎたため軟化しすぎて引張強さが低下してしまった。   Furthermore, 1H was too soft because the final annealing temperature was too high, and the tensile strength decreased.
さらに、試料番号3A〜10Aの最終焼鈍板は、この発明で規定する製造工程条件は満たしているが、成分組成条件を満たさない比較例である。   Furthermore, the final annealed plates of sample numbers 3A to 10A are comparative examples that satisfy the manufacturing process conditions defined in the present invention but do not satisfy the component composition conditions.
3AはSi量が、5AはMg量が、7AはCu量がそれぞれ少なすぎたため引張強さが低下してしまった。   3A had an Si content, 5A had an Mg content, and 7A had an excessively small Cu content.
また4AはSi量が、6AはMg量が、8AはCu量がそれぞれ多すぎたため導電率が低下してしまったとともに、4Aは曲げ加工性も劣化してしまった。   Further, 4A had an Si content, 6A had an Mg content, and 8A had an excessive Cu content, so that the electrical conductivity was lowered and 4A was also deteriorated in bending workability.
また9AはTi量とB量が多すぎたため初晶AlTiの晶出やTiBが生成し、10AはFe量が多すぎたためAl-Fe系金属間化合物のサイズが大きくなって、両者の曲げ加工性は劣化してしまったとともに、導電率も低下してしまった。 In addition, since 9A has too much Ti and B, crystallization of primary Al 3 Ti and TiB 2 is generated, and 10A has too much Fe, so the size of the Al—Fe intermetallic compound is increased. In addition to the deterioration of the bending workability, the electrical conductivity also decreased.

Claims (2)

  1. Si1.1〜1.5%(mass%、以下同じ)、Mg0.3〜0.6%、Cu0.6〜0.8%を含有し、さらにTi0.005〜0.15%を単独であるいはB0.0001〜0.05%と共に含有し、不純物としてのFeを0.35%以下に規制し、残部がAlおよび不可避的不純物よりなり、かつ導電率が55%IACS以上、引張強さが215N/mm以上であることを特徴とする、熱伝導性と強度と曲げ加工性に優れたアルミニウム合金圧延板 Si 1.1 to 1.5% (mass%, the same shall apply hereinafter), Mg 0.3 to 0.6%, Cu 0.6 to 0.8%, and Ti 0.005 to 0.15% alone or B is contained together with 0.0001-0.05%, Fe as an impurity is regulated to 0.35% or less, the balance is made of Al and unavoidable impurities, the conductivity is 55% IACS or more, and the tensile strength is 215N / Mm 2 or more aluminum alloy rolled plate excellent in thermal conductivity, strength and bending workability
  2. 請求項1記載の化学組成を有するアルミニウム合金の鋳塊に、500〜570℃の範囲内の温度で1〜24時間の均質化処理を施し、次いで熱間圧延を450℃以上の温度で開始し300℃以下で終了し、さらに60%以上の圧延率で冷間圧延を施した後、140〜200℃の最終焼鈍を施し、これにより最終焼鈍板の導電率が55%IACS以上、引張強さが215N/mm以上とすることを特徴とする、熱伝導性と強度と曲げ加工性に優れたアルミニウム合金圧延板の製造方法。 The aluminum alloy ingot having the chemical composition according to claim 1 is subjected to a homogenization treatment at a temperature in the range of 500 to 570 ° C for 1 to 24 hours, and then hot rolling is started at a temperature of 450 ° C or higher. After finishing at 300 ° C. or lower and further cold rolling at a rolling rate of 60% or higher, the final annealing at 140 to 200 ° C. is performed. The manufacturing method of the aluminum alloy rolled sheet excellent in thermal conductivity, intensity | strength, and bending workability characterized by being 215 N / mm < 2 > or more.
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