JP2019189907A - Al-Si-Mg-BASED ALUMINUM ALLOY SHEET - Google Patents
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 70
- 239000011856 silicon-based particle Substances 0.000 claims abstract description 44
- 229910018566 Al—Si—Mg Inorganic materials 0.000 claims abstract description 25
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 16
- 239000011777 magnesium Substances 0.000 claims abstract description 16
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 15
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 15
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 13
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims abstract description 12
- 239000010703 silicon Substances 0.000 claims abstract description 12
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 8
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims abstract description 7
- 238000005096 rolling process Methods 0.000 claims description 23
- 229910052751 metal Inorganic materials 0.000 claims description 14
- 239000002184 metal Substances 0.000 claims description 14
- 239000010949 copper Substances 0.000 claims description 10
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 7
- 229910052802 copper Inorganic materials 0.000 claims description 7
- 239000000463 material Substances 0.000 abstract description 13
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- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 description 2
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
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- 229910052719 titanium Inorganic materials 0.000 description 2
- 229910021364 Al-Si alloy Inorganic materials 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 229910001111 Fine metal Inorganic materials 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 229910004298 SiO 2 Inorganic materials 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- XLOMVQKBTHCTTD-UHFFFAOYSA-N Zinc monoxide Chemical compound [Zn]=O XLOMVQKBTHCTTD-UHFFFAOYSA-N 0.000 description 1
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- 239000010935 stainless steel Substances 0.000 description 1
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- JBQYATWDVHIOAR-UHFFFAOYSA-N tellanylidenegermanium Chemical compound [Te]=[Ge] JBQYATWDVHIOAR-UHFFFAOYSA-N 0.000 description 1
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Abstract
Description
本発明は、Ａｌ−Ｓｉ−Ｍｇ系アルミニウム合金板に係り、更に詳細には、ケイ素（Ｓｉ）を多く含有するアルミニウムスクラップ材を利用可能な、高強度で成形性に優れるＡｌ−Ｓｉ−Ｍｇ系アルミニウム合金板に関する。 The present invention relates to an Al-Si-Mg-based aluminum alloy plate, and more specifically, an Al-Si-Mg-based high-strength and excellent formability capable of using an aluminum scrap material containing a large amount of silicon (Si). It relates to an aluminum alloy plate.
従来から、自動車、船舶、航空機などの輸送機や、機械、電気製品、建築、構造物、光学機器等の部材や部品用として各種アルミニウム合金板が用いられており、それぞれの用途に応じて種々の特性を有するアルミニウム合金の開発が行われている。 Conventionally, various aluminum alloy plates have been used for members and parts of transportation equipment such as automobiles, ships, aircraft, machines, electrical products, architecture, structures, optical equipment, etc. An aluminum alloy having the following characteristics has been developed.
自動車業界においては、大気汚染や地球温暖化に対処するため、車体等の軽量化により燃費を向上させ、排出する二酸化炭素量を低減させることが行われており、アルミニウム合金板が多用される。 In the automobile industry, in order to cope with air pollution and global warming, it is carried out to reduce fuel consumption and reduce the amount of carbon dioxide emitted by reducing the weight of a vehicle body, and aluminum alloy plates are frequently used.
アルミニウム合金板は、一般的にプレス成形等によって自動車用部品に成形されるため、伸び性がよく高い成形性を有することが要求されると共に、自動車用部品としての高い強度、耐力を有することが要求される。 Since aluminum alloy plates are generally formed into automotive parts by press molding or the like, they are required to have good extensibility and high formability, and have high strength and proof strength as automotive parts. Required.
特許文献１の特許第５４２３８２２号公報には、マグネシウム（Ｍｇ）含有量を増加させて、微細なサブグレイン組織を形成させることで高温高速成形時に高い伸びが得られるアルミニウム合金板を製造できる旨が開示されている。
Japanese Patent No. 5423822 of
近年においては、資源枯渇、廃棄処分場残存容量等の観点から、資源循環型社会構築の必要性が高まっている。そして、アルミニウムスクラップ材を再生する場合のエネルギー量は、新しく地金を製造する場合のエネルギー量よりも格段に少ないため、アルミニウムスクラップ材の積極的な利用が望まれる。 In recent years, the necessity of building a resource recycling society is increasing from the viewpoints of resource depletion, remaining capacity of disposal sites, and the like. And since the energy amount at the time of reproducing | regenerating an aluminum scrap material is remarkably smaller than the energy amount at the time of manufacturing a new metal, the positive utilization of an aluminum scrap material is desired.
しかし、アルミニウムのスクラップ材は、アルミナから製錬された新地金とは異なり、砂塵（ＳｉＯ２）由来のケイ素（Ｓｉ）や、シュレッダーなどのスクラップ処理施設で混入する鉄（Ｆｅ）等の不純物を多く含む。 However, unlike scrap metal smelted from alumina, aluminum scrap materials contain impurities such as silicon (Si) derived from dust (SiO 2 ) and iron (Fe) mixed in scrap processing facilities such as shredders. Including many.
上記Ａｌ−Ｓｉ系合金は、固溶限度を超えるＳｉを含有し、マトリックス中に薄く硬い板状結晶のＳｉ粒子が析出するため、上記Ｓｉ粒子に引張応力が集中し切欠き効果によって伸び率が低下する。 The Al-Si alloy contains Si exceeding the solid solution limit, and thin and hard plate-like Si particles are precipitated in the matrix. Therefore, tensile stress is concentrated on the Si particles, and the elongation rate is increased by a notch effect. descend.
そして、上記板状のＳｉ粒子は、圧延により図１に示すように一方向に配列するため、圧延したアルミニウム合金板は、圧延直角方向の伸び率が著しく低下し、伸び異方性が生じてプレス成形性が低下する。つまり、アルミニウム合金板のプレス成形性は、最も伸び難い方向の伸び率の影響を受ける。
図１中、伸び率の大きさを矢印の長さで示した。
And since the plate-like Si particles are arranged in one direction by rolling as shown in FIG. 1, the rolled aluminum alloy plate has a significantly reduced elongation in the direction perpendicular to the rolling, and anisotropy of elongation occurs. Press formability decreases. That is, the press formability of the aluminum alloy plate is affected by the elongation rate in the direction in which it is most difficult to stretch.
In FIG. 1, the magnitude of elongation is indicated by the length of the arrow.
本発明は、このような従来技術の有する課題に鑑みてなされたものであり、その目的とするところは、Ｓｉ含有量が多いアルミニウムスクラップ材を利用しても、伸び異方性が小さくプレス成形性に優れ、自動車用部品に要求される耐力を有するＡｌ−Ｓｉ−Ｍｇ系アルミニウム合金板を提供することにある。 The present invention has been made in view of the above-described problems of the prior art, and the object of the present invention is to provide press forming with a small elongation anisotropy even when an aluminum scrap material having a high Si content is used. An object of the present invention is to provide an Al—Si—Mg-based aluminum alloy sheet that has excellent properties and has the yield strength required for automotive parts.
本発明者は、上記目的を達成すべく鋭意検討を重ねた結果、不可避的に析出・晶出するケイ素（Ｓｉ）粒子による切欠き効果を低減させると共に、上記Ｓｉ粒子を均一に微分散させることで、上記目的が達成できることを見出し、本発明を完成するに至った。 As a result of intensive studies to achieve the above object, the present inventor reduces the notch effect due to inevitably precipitated and crystallized silicon (Si) particles and uniformly finely disperses the Si particles. Thus, the inventors have found that the above object can be achieved and have completed the present invention.
即ち、本発明のＡｌ−Ｓｉ−Ｍｇ系アルミニウム合金板は、アルミニウム（Ａｌ）を主成分とし、４質量％以上７質量％以下のケイ素（Ｓｉ）と、０．３質量％以上０．８質量％以下のマグネシウム（Ｍｇ）と、を含有し、残部が、０．６質量％以下の鉄（Ｆｅ）と不可避不純物とから成る。
そして、Ｓｉ粒子の平均最大長が２．０μｍ以下であり、上記Ｓｉ粒子を母点としてボロノイ分割したセルの平均面積が２６μｍ２以下、かつ上記セルの面積の変動係数が０．９以下である金属組織を有し、耐力が１００ＭＰａ以上であることを特徴とする。
That is, the Al—Si—Mg-based aluminum alloy plate of the present invention contains aluminum (Al) as a main component, 4 mass% to 7 mass% silicon (Si), and 0.3 mass% to 0.8 mass%. % Or less of magnesium (Mg), and the balance is made up of 0.6% by mass or less of iron (Fe) and inevitable impurities.
The average maximum length of the Si particles is 2.0 μm or less, the average area of the Voronoi-divided cell using the Si particles as a base point is 26 μm 2 or less, and the variation coefficient of the area of the cell is 0.9 or less. It has a metal structure and has a proof stress of 100 MPa or more.
本発明によれば、Ａｌ−Ｓｉ−Ｍｇ系アルミニウム合金板において、Ｓｉ粒子の平均最大長を２．０μｍ以下にしてＳｉ粒子による切欠き効果を低減させ、さらに、上記Ｓｉ粒子が均一に微分散した金属組織を形成したため、伸び異方性が小さくプレス成形性に優れるＡｌ−Ｓｉ−Ｍｇ系アルミニウム合金板を提供することができる。 According to the present invention, in the Al—Si—Mg-based aluminum alloy plate, the average maximum length of the Si particles is set to 2.0 μm or less to reduce the notch effect due to the Si particles, and the Si particles are uniformly finely dispersed. Since the formed metal structure is formed, an Al—Si—Mg-based aluminum alloy plate having a small elongation anisotropy and excellent press formability can be provided.
＜アルミニウム合金板＞
本発明のアルミニウム合金板について詳細に説明する。
上記アルミニウム合金板は、Ａｌ−Ｓｉ−Ｍｇ系のアルミニウム合金板であり、アルミニウム（Ａｌ）を主成分とし、４質量％以上７質量％以下のケイ素（Ｓｉ）と、０．３質量％以上０．８質量％以下のマグネシウム（Ｍｇ）と、を含有し、残部が、０．６質量％以下の鉄（Ｆｅ）と不可避不純物とから成る。
<Aluminum alloy plate>
The aluminum alloy plate of the present invention will be described in detail.
The aluminum alloy plate is an Al—Si—Mg based aluminum alloy plate, mainly composed of aluminum (Al), 4 mass% to 7 mass% silicon (Si), 0.3 mass% to 0 mass%. 0.8 mass% or less of magnesium (Mg), and the balance is made up of 0.6 mass% or less of iron (Fe) and inevitable impurities.
一般に、Ａｌ−Ｓｉ−Ｍｇ系のアルミニウム合金板は、薄く硬い板状結晶のＳｉ粒子が析出するため、上記のように、Ｓｉ粒子による切欠き効果によって伸びが妨げられてプレス成形性が低下する。 In general, Al—Si—Mg-based aluminum alloy plates have thin and hard plate-like crystal Si particles precipitated, and as described above, the notch effect due to the Si particles prevents the stretch and lowers the press formability. .
本発明のアルミニウム合金板は、その金属組織が、マトリックス相中に含まれるＳｉ粒子の平均最大長が２．０μｍ以下であり、上記Ｓｉ粒子を母点としてボロノイ分割したセルの平均面積が２６μｍ２以下、かつ上記セルの面積の変動係数が０．９以下である。 In the aluminum alloy plate of the present invention, the metal structure has an average maximum length of Si particles contained in the matrix phase of 2.0 μm or less, and an average area of cells obtained by Voronoi division using the Si particles as a base point is 26 μm 2. The variation coefficient of the cell area is 0.9 or less.
マトリックス相中に析出したＳｉ粒子の平均最大長が２．０μｍ以下であることで、Ｓｉ粒子による切欠き効果が小さくなってアルミニウム合金板の伸び率が向上する。
さらに、上記Ｓｉ粒子の平均最大長が１．８μｍ以下であると、個々のＳｉ粒子による切欠き効果がさらに小さくなって伸び率がより向上する。
When the average maximum length of the Si particles precipitated in the matrix phase is 2.0 μm or less, the notch effect due to the Si particles is reduced and the elongation of the aluminum alloy plate is improved.
Further, when the average maximum length of the Si particles is 1.8 μm or less, the notch effect by the individual Si particles is further reduced, and the elongation rate is further improved.
加えて、上記Ｓｉ粒子を母点としてボロノイ分割したセルの面積の変動係数が０．９以下であり、かつその平均面積が２６μｍ２以下である金属組織を有する。 In addition, it has a metal structure in which the variation coefficient of the area of the cell obtained by Voronoi division using the Si particles as a base point is 0.9 or less and the average area is 26 μm 2 or less.
ボロノイ分割とは、図２に示すように、隣り合う母点間を結ぶ直線の垂直二等分線を引き、各母点の最近隣領域を分割してボロノイ図を作成する手法である。
また、上記変動係数は、標準偏差（σ）を平均値で割った無次元の値であり、本発明においては、上記セルの大きさが平均値に対してどの程度するバラツキいているかを表わす。
The Voronoi division is a method of creating a Voronoi diagram by drawing a perpendicular bisector of a straight line connecting adjacent generating points and dividing the nearest neighbor region of each generating point, as shown in FIG.
The variation coefficient is a dimensionless value obtained by dividing the standard deviation (σ) by the average value. In the present invention, the variation coefficient represents how much the cell size varies with respect to the average value.
上記アルミニウム合金板の金属組織は、Ｓｉ粒子間の垂直二等分線で囲まわれたセルの面積が小さく、Ｓｉ粒子数が多くその粒子径が小さいため、個々のＳｉ粒子による切欠き効果が小さい。 The metal structure of the aluminum alloy plate has a small cell area surrounded by vertical bisectors between Si particles, and since the number of Si particles is large and the particle diameter is small, the notch effect by individual Si particles is small. .
さらに、上記セルの大きさのバラツキが小さく、個々のＳｉ粒子が凝集せずに間隔をあけて均一に分散しているため、多数のＳｉ粒子が配列したり凝集したりして、特定方向の伸びを妨げることがなく、上記切欠き効果の小ささと相俟って、伸び異方性が抑制され、優れたプレス成形性を有する。 Furthermore, since the variation in the cell size is small, and the individual Si particles are uniformly dispersed at intervals without agglomeration, a large number of Si particles are arranged or agglomerated, so Elongation is not hindered and coupled with the small notch effect, elongation anisotropy is suppressed and excellent press formability is achieved.
上記セルの平均面積は、２３．６μｍ２以下であることが好ましく、２１μｍ２以下であることがより好ましい。上記セルの面積が小さく、Ｓｉ粒子数が多くなってその粒子が小さくなると、上記変動係数と相俟って、さらに伸び率が向上し、等方的に伸びるようになる。 Average area of the cell is preferably not 23.6Myuemu 2 or less, more preferably 21 [mu] m 2 or less. When the area of the cell is small and the number of Si particles is increased and the particles are reduced, the elongation rate is further improved and isotropically extended in combination with the coefficient of variation.
また、上記Ｓｉ粒子のアスペクト比は、１．０〜１．６であることが好ましい。本発明においてはＳｉ粒子を微細化しているため、Ｓｉ粒子の形状が伸びに及ぼす影響は小さいが、アスペクト比が上記範囲内であることで、伸び異方性を低減できる。 The aspect ratio of the Si particles is preferably 1.0 to 1.6. In the present invention, since the Si particles are miniaturized, the influence of the shape of the Si particles on the elongation is small, but when the aspect ratio is within the above range, the elongation anisotropy can be reduced.
上記Ｓｉ粒子の最大長、Ｓｉ粒子のアスペクト比、ボロノイ分割したセルの平均面積、および、その変動係数は、アルミニウム合金板の光学顕微鏡写真を画像処理することで算出できる。 The maximum length of the Si particles, the aspect ratio of the Si particles, the average area of the Voronoi-divided cells, and the coefficient of variation thereof can be calculated by image processing of an optical micrograph of the aluminum alloy plate.
本発明においては、光学顕微鏡写真２１２．８×１６１．４μｍの観察視野を４００倍に拡大（２５８８×１９６２ｐｉｘｃｅｌ）し、解析ソフト（Ｉｍａｇｅ Ｊ １．５０ｉ）を用い、色閾値をＤｅｆａｕｌｔで二値化して最大長が０．５μｍ以上のＳｉ粒子を抽出して求めた。 In the present invention, the observation field of the optical micrograph 212.8 × 161.4 μm is magnified 400 times (2588 × 1962 pixels), and the color threshold is binarized by default using analysis software (Image J 1.50i). Then, Si particles having a maximum length of 0.5 μm or more were extracted and determined.
上記アルミニウム合金板は、圧延方向（ＲＤ）と圧延直角方向（ＴＤ）の伸び比（ＲＤ／ＴＤ）が、０．８以上１．２以下であり、伸び率が２０％以上であることが好ましい。
アルミニウム合金板が上記範囲の伸びを示し、伸び異方性が小さいことでプレス成形性が優れ、自動車部品に好適に使用できる。
The aluminum alloy sheet preferably has an elongation ratio (RD / TD) in the rolling direction (RD) and the direction perpendicular to the rolling direction (TD) of 0.8 to 1.2 and an elongation of 20% or more. .
The aluminum alloy plate exhibits an elongation in the above range, and since the elongation anisotropy is small, the press formability is excellent and can be suitably used for automobile parts.
本発明において「伸び率」は、アルミニウム合金板を引っ張り、破断したときの長さ（Ｌ＋ΔＬ）と、元の長さ（Ｌ）との比（ΔＬ／Ｌ ×１００）で表され、単に伸び率というときは、伸びが小さい方向の伸び率を意味する。 In the present invention, the “elongation rate” is represented by the ratio (ΔL / L × 100) between the length (L + ΔL) when the aluminum alloy plate is pulled and broken and the original length (L), and is simply the elongation rate. When it says, it means the elongation in the direction of small elongation.
上記アルミニウム合金板は、耐力が１００ＭＰａ以上である。アルミニウム合金板が高い耐力を有することで、自動車用部品に好適に使用できる。 The aluminum alloy plate has a yield strength of 100 MPa or more. Since the aluminum alloy plate has a high yield strength, it can be suitably used for automotive parts.
次に、Ａｌ−Ｓｉ−Ｍｇ系アルミニウム合金板の金属組成について説明する。
本発明のＡｌ−Ｓｉ−Ｍｇ系アルミニウム合金板は、アルミニウム（Ａｌ）を主成分とする。本発明において「主成分」とは８０質量％以上含有する成分をいう。
Next, the metal composition of the Al—Si—Mg based aluminum alloy plate will be described.
The Al—Si—Mg-based aluminum alloy plate of the present invention contains aluminum (Al) as a main component. In the present invention, the “main component” refers to a component containing 80% by mass or more.
上記アルミニウム合金板は、ケイ素（Ｓｉ）を４質量％以上７質量％以下含む。
ケイ素は、砂塵の混入や、サッシ屑やロードホイール等のアルミニウムスクラップ材に多く含まれ、ケイ素を含有するアルミニウム合金板とすることでアルミニウムスクラップ材を有効に利用できる。
The aluminum alloy plate contains 4% by mass to 7% by mass of silicon (Si).
Silicon is abundantly contained in aluminum dust materials such as dust and sash scraps and road wheels. By using silicon-containing aluminum alloy plates, aluminum scrap materials can be used effectively.
アルミニウム合金板がケイ素を含有することで、板材鋳造時の湯流れ性が向上し、アルミニウム合金板の耐力及び引張強さが向上する。
ケイ素の含有量が４質量％未満では、マトリックス中に析出するＳｉ粒子が少なく、伸び異方性の問題は生じ難いが、鋳造時の流動性が低下することがあり、７質量％を超えると、２０％以上の伸びが得られず成形性が低下することがある。
When the aluminum alloy plate contains silicon, the flowability of the hot water during casting of the plate material is improved, and the proof stress and tensile strength of the aluminum alloy plate are improved.
When the silicon content is less than 4% by mass, the amount of Si particles precipitated in the matrix is small, and the problem of elongation anisotropy is unlikely to occur. However, the fluidity during casting may be reduced. , 20% or more elongation may not be obtained, and moldability may be reduced.
上記アルミニウム合金板は、マグネシウム（Ｍｇ）を０．３質量％以上０．８質量％以下含む。
マグネシウムは固溶強化元素であり、Ｍｇを０．３質量％以上含有し、マトリックス中に固溶させることでアルミニウム合金板の耐力及び引張強さ、伸びを向上させることができる。また、Ｍｇの含有量が０．８質量％を超えるとマトリックス中に析出して、伸びが低下することがある。
The said aluminum alloy plate contains 0.3 mass% or more and 0.8 mass% or less of magnesium (Mg).
Magnesium is a solid solution strengthening element. It contains 0.3 mass% or more of Mg, and the proof stress, tensile strength, and elongation of the aluminum alloy plate can be improved by solid solution in the matrix. On the other hand, if the Mg content exceeds 0.8% by mass, it may precipitate in the matrix and the elongation may decrease.
上記アルミニウム合金板の鉄（Ｆｅ）の含有量は、０．６質量％以下である。
アルミニウム合金板がＦｅを含有することで鋳造時の焼付き性が向上するが、Ｆｅの含有量が０．６質量％を超えると、プレス成形性が低下することがある。
The iron (Fe) content of the aluminum alloy plate is 0.6% by mass or less.
Although the seizure property at the time of casting improves because an aluminum alloy plate contains Fe, when the content of Fe exceeds 0.6 mass%, press formability may be reduced.
鉄は、ステンレス鋼や鉄粉がスクラップ処理施設で混入し易いため、アルミニウムスクラップ材に多く含まれるものであり、鉄を含有するアルミニウム合金板とすることでアルミニウムスクラップ材を有効に利用できる。 Since iron is easily mixed in stainless steel and iron powder at a scrap processing facility, iron is often contained in aluminum scrap material, and aluminum scrap material can be effectively used by using an aluminum alloy plate containing iron.
さらに、上記アルミニウム合金板は、銅（Ｃｕ）を０．０１質量％以上１．２質量％以下含むことが好ましく、さらに０．２質量％以上１．２質量％以下含むことがより好ましい。アルミニウム合金板のマトリックス中に銅をマトリックス中に固溶させることで耐力及び引張強さ、伸びを向上させることができる。 Furthermore, it is preferable that the said aluminum alloy plate contains 0.01 mass% or more and 1.2 mass% or less of copper (Cu), and also more preferably contains 0.2 mass% or more and 1.2 mass% or less. Yield strength, tensile strength, and elongation can be improved by dissolving copper in the matrix of the aluminum alloy plate.
Ｃｕの含有量が１．２質量％を超えると、２０％以上の伸びが得られずプレス成形性が低下することがあり、また耐食性が低下することがある。なお、銅は、銅線やダイカスト部品等から混入することが多い。 If the Cu content exceeds 1.2% by mass, an elongation of 20% or more cannot be obtained, and press formability may be lowered, and corrosion resistance may be lowered. Copper is often mixed from copper wires, die cast parts, and the like.
上記不可避的不純物としては、例えば、マンガン（Ｍｎ）、チタン（Ｔｉ）、クロム（Ｃｒ）、亜鉛（Ｚｎ）等が挙げられる。
これらの含有量は少ないことが好ましく、これら不可避的不純物の含有量は、Ｍｎは０．６質量％以下、Ｔｉは０．２質量％以下、Ｚｎは０．３質量％以下、その他、Ｃｒ、Ｎｉ, Ｐｂ、Ｓｎ等は各０．０５質量％以下であることが好ましい。
Examples of the inevitable impurities include manganese (Mn), titanium (Ti), chromium (Cr), and zinc (Zn).
These contents are preferably small, and the contents of these inevitable impurities are Mn 0.6 mass% or less, Ti 0.2 mass% or less, Zn 0.3 mass% or less, Cr, Ni, Pb, Sn and the like are each preferably 0.05% by mass or less.
＜製造方法＞
本発明のＡｌ−Ｓｉ−Ｍｇ系アルミニウム合金板の製造方法について説明する。
上記アルミニウム合金板は、縦型双ロールキャスト式による連続鋳造法により鋳造板を作製し、該鋳造板を冷間圧延し、焼鈍、急冷することで作製できる。
<Manufacturing method>
The manufacturing method of the Al-Si-Mg type aluminum alloy plate of this invention is demonstrated.
The aluminum alloy plate can be produced by producing a cast plate by a continuous casting method using a vertical twin-roll cast method, cold rolling, annealing and rapidly cooling the cast plate.
（鋳造板の作製）
縦型双ロールキャスト式による連続鋳造法は、図３に示すように、回転する一対の冷却された双ロールの間に、耐火物製の給湯ノズルにアルミニウム合金溶湯を注湯し、上記双ロール間で圧下すると共に急冷して、アルミニウム合金の鋳造板を作製する方法である。縦型の双ロールキャストは、ロール間隙において固相率が変化し難くアルミニウム合金溶湯が詰まり難い。
(Production of cast plate)
As shown in FIG. 3, the continuous casting method by the vertical twin roll cast method involves pouring a molten aluminum alloy into a refractory hot water supply nozzle between a pair of rotating twin rolls rotating, This is a method for producing an aluminum alloy cast plate by rolling down and quenching. In the vertical twin roll cast, the solid phase ratio hardly changes in the gap between the rolls, and the molten aluminum alloy does not easily clog.
縦型双ロールキャスト法の冷却速度は、従来のＤＣ鋳造法やベルト式連続鋳造法に比して１〜３桁大きい。このため、得られるアルミニウム合金板の金属組織が微細になり、プレス成形性などの加工性に優れたアルミニウム合金板を得ることができる。 The cooling rate of the vertical twin roll casting method is 1 to 3 orders of magnitude higher than that of the conventional DC casting method or belt type continuous casting method. For this reason, the metal structure of the obtained aluminum alloy plate becomes fine, and an aluminum alloy plate excellent in workability such as press formability can be obtained.
本発明においては銅又は銅合金のロールを用いる。熱伝導率が高いロールを用いることで冷却性能がさらに向上する。具体的には３００℃未満に冷却されて、粗大なＳｉ粒子が析出し難く、晶出物が微細分散するため、不純物による伸び率低下を防止できる。 In the present invention, a copper or copper alloy roll is used. Cooling performance is further improved by using a roll having high thermal conductivity. Specifically, since it is cooled to less than 300 ° C., coarse Si particles are hardly precipitated, and the crystallized product is finely dispersed, so that it is possible to prevent a decrease in elongation due to impurities.
なお、ＤＣ鋳造などで鋳造した鋳塊を均熱処理後に熱間圧延を行う通常の製造方法では、鋳造の際の鋳塊にＳｉ、Ｍｇ、Ｆｅ等が偏析するため、通常の熱間圧延では、Ａｌ−Ｓｉ−Ｍｇ系アルミニウム合金の延性が著しく低下して割れが発生するため、加工すること自体が困難である。 In addition, in a normal manufacturing method in which an ingot cast by DC casting or the like is hot-rolled after soaking, Si, Mg, Fe, etc. segregate in the ingot at the time of casting. Since the ductility of the Al—Si—Mg-based aluminum alloy is significantly lowered and cracks are generated, it is difficult to process the Al—Si—Mg based aluminum alloy.
上記双ロールの表面は潤滑されていないことが好ましい。酸化物粉末（アルミナ粉、酸化亜鉛粉等）、ＳｉＣ粉末、グラファイト粉末、油、溶融ガラスなどの潤滑剤を双ロール表面に供給すると冷却速度が遅くなり、結晶粒が粗大化してアルミニウム合金板の成形性が低下することがある。また、潤滑剤の濃度や厚みの不均一による冷却のムラが防止され、均一かつ充分な冷却速度が得られ、偏析が防止されて成形性を均一にすることができる。 The surface of the twin roll is preferably not lubricated. When a lubricant such as oxide powder (alumina powder, zinc oxide powder, etc.), SiC powder, graphite powder, oil, molten glass, etc. is supplied to the twin roll surface, the cooling rate becomes slow, the crystal grains become coarse and the aluminum alloy plate Formability may be reduced. Further, uneven cooling due to uneven concentration and thickness of the lubricant is prevented, a uniform and sufficient cooling rate is obtained, segregation is prevented, and formability can be made uniform.
上記双ロールに注湯するアルミニウム合金溶湯の注湯温度は、液相線温度＋５℃以上とすることが好ましい。液相線温度＋５℃未満では成形時の固相率が高くなり、空気の巻き込み、または板厚中心相などのＳｉ濃度が高くなり、冷間圧延性や成形性の低下が生じることがある。また、冷却速度が９００℃／秒以上であれば、注湯温度が高くても構わないが、液相線温度＋３０℃以下であることが好ましい。 The pouring temperature of the molten aluminum alloy poured into the twin rolls is preferably set to the liquidus temperature + 5 ° C or higher. If the liquidus temperature is less than + 5 ° C., the solid phase ratio during molding increases, and the Si concentration in the air entrainment or the plate thickness center phase increases, which may result in a decrease in cold rollability and formability. Moreover, if the cooling rate is 900 ° C./second or more, the pouring temperature may be high, but the liquidus temperature is preferably + 30 ° C. or less.
冷却速度が低下すると、金属間化合物等が粗大化したり、多量に晶出したりすることがあり、強度伸びバランスが低下し、プレス成形性が著しく低下することがある。
また、双ロールの圧下効果が小さくなって中心欠陥が多くなり、アルミニウム合金板の基本的な機械的性質が低下することがある。
When the cooling rate is lowered, the intermetallic compound or the like may be coarsened or crystallized in a large amount, the strength elongation balance may be lowered, and the press formability may be significantly lowered.
In addition, the rolling effect of the twin rolls is reduced, the number of center defects is increased, and the basic mechanical properties of the aluminum alloy sheet may be deteriorated.
上記双ロールを回転させるときの周速は、０．９ｍ／ｓｅｃ以上とすることが好ましい。
ロールの周速が０．９ｍ／ｓｅｃ未満では、アルミニウム合金溶湯とロールとの接触時間が長くなり、鋳造板の表面品質が低下することがある。また、周速が速すぎると、充分凝固できず表面や内部に欠陥が生じやすくなり、実用板材として充分な品質が確保できない可能性がある。
The peripheral speed when rotating the twin rolls is preferably 0.9 m / sec or more.
When the peripheral speed of the roll is less than 0.9 m / sec, the contact time between the molten aluminum alloy and the roll becomes long, and the surface quality of the cast plate may be deteriorated. On the other hand, if the peripheral speed is too high, it cannot be sufficiently solidified and defects are easily generated on the surface and inside, and there is a possibility that sufficient quality as a practical plate material cannot be ensured.
本発明では、必要に応じて、前記双ロールに注湯後に、双ロール間で凝固しつつある板状鋳塊に対して、双ロールによって、３００ｋＮ／ｍ以下の圧下荷重を負荷しつつ鋳造してもよい。 In the present invention, if necessary, after pouring into the twin rolls, the plate ingot that is solidified between the twin rolls is cast by applying a rolling load of 300 kN / m or less by the twin rolls. May be.
上記圧下荷重の負荷によって、注湯時や凝固中に発生したガスが、板状鋳片内から外部に放出されやすくなり、空隙の発生が抑制される。そして、後述する冷間圧延と相俟って空隙等の鋳造欠陥の量を、成形特性に影響を及ぼすことがない範囲にまで抑制することができる。 By the load of the rolling load, the gas generated during pouring or during solidification is easily released to the outside from the plate-shaped slab, and the generation of voids is suppressed. And the quantity of casting defects, such as a space | gap, combined with the cold rolling mentioned later, can be suppressed to the range which does not affect a shaping | molding characteristic.
縦型双ロールキャスト式による連続鋳造法により、１〜９ｍｍの鋳造板を作製することが好ましい。鋳造板の板厚を１〜９ｍｍとすることで熱間粗圧延、熱間仕上げ圧延等の工程を省略することができ、生産性を向上させることができる。 It is preferable to produce a cast plate of 1 to 9 mm by a continuous casting method using a vertical twin roll cast method. By setting the thickness of the cast plate to 1 to 9 mm, steps such as hot rough rolling and hot finish rolling can be omitted, and productivity can be improved.
（冷間圧延）
本発明においては、上記双ロールキャスト式による連続鋳造法で作製された鋳造板に対して冷間圧延を行う。冷間圧延することで鋳造板中の結晶粒を微細化することができる。
(Cold rolling)
In the present invention, cold rolling is performed on a cast plate produced by the continuous casting method using the twin roll cast method. By cold rolling, the crystal grains in the cast plate can be refined.
冷間圧延の圧下率（（冷間圧延前の板厚−冷間圧延後の板厚）／冷間圧延前の板厚×１００）は、冷間圧延を１回で行う場合は７５％以上９０％以下であることが好ましい。 Cold rolling reduction ratio ((sheet thickness before cold rolling−sheet thickness after cold rolling) / sheet thickness before cold rolling × 100) is 75% or more when cold rolling is performed once. It is preferable that it is 90% or less.
また、後述する焼鈍を挟んで冷間圧延を複数回行う場合は、合計の圧下率が６０％以上９０％以下であることが好ましい。 In addition, when cold rolling is performed a plurality of times with annealing described later, the total rolling reduction is preferably 60% or more and 90% or less.
冷間圧延の圧下率を上記範囲にすることで、マトリックス中に析出したＳｉ粒子を粉砕して微細化すると共に、マトリックス中の微細なＳｉ粒子同士を引き離してＳｉ粒子の間隔を広げ、Ｓｉ粒子を母点としてボロノイ分割したセルの平均面積を小さくし、かつその面積の変動係数を小さくできる。 By making the rolling reduction of the cold rolling within the above range, the Si particles precipitated in the matrix are pulverized and refined, and the fine Si particles in the matrix are separated from each other to increase the spacing between the Si particles. Thus, the average area of the Voronoi-divided cells can be reduced with the variation point of the area being reduced.
（焼鈍）
焼鈍は、５００℃以上液相線温度以下の温度範囲で行う。具体的には、５２０℃〜５５０℃で１時間以上焼鈍を行うことが好ましい。
上記の条件で焼鈍することで、上記冷間圧延で粉砕された微細なＳｉ粒子が部分的にマトリックス中に溶け込み、その外形が小さくなると共に、丸くなってＳｉ粒子の間隔が広がる。さらに、マトリックス中に溶け込んでない他の元素が、マトリックス中に固溶して、耐力を向上させることができる。焼鈍は、バッチ式の空気炉や連続式の処理炉で行うことができる。
(Annealing)
Annealing is performed in a temperature range of 500 ° C. or higher and a liquidus temperature or lower. Specifically, it is preferable to perform annealing at 520 ° C. to 550 ° C. for 1 hour or longer.
By annealing under the above conditions, the fine Si particles pulverized by the cold rolling partially dissolve in the matrix, the outer shape becomes smaller, and the shape becomes round and the interval between the Si particles increases. Furthermore, other elements not dissolved in the matrix can be dissolved in the matrix to improve the proof stress. Annealing can be performed in a batch type air furnace or a continuous processing furnace.
（急冷）
本発明のアルミニウム合金板は、上記焼鈍した後、直ちに急冷を行う。焼鈍によって得られた固溶状態を急速に冷却して過飽和固溶体とすることで、室温においても、高温と同じような結晶状態を保つことができ、耐力が向上する。
(Rapid cooling)
The aluminum alloy plate of the present invention is immediately cooled immediately after the annealing. By rapidly cooling the solid solution obtained by annealing to form a supersaturated solid solution, a crystalline state similar to the high temperature can be maintained even at room temperature, and the proof stress is improved.
急冷の冷却速度はできるだけ速いことが好ましく、具体的には、板材を水に入れる水冷法により行い、１００℃／ｓｅｃ以上で冷却することが好ましい。冷却温度が遅いと、良好な過飽和固溶体が形成されずに耐力が低下する。 The rapid cooling rate is preferably as fast as possible. Specifically, it is preferable to cool the plate at 100 ° C./sec or more by a water cooling method in which a plate material is put into water. When the cooling temperature is slow, a good supersaturated solid solution is not formed and the yield strength is lowered.
＜自動車部品＞
本発明のＡｌ−Ｓｉ−Ｍｇ系アルミニウム合金板は、耐力が１００ＭＰａ以上、伸びが２０％以上であり、自動車用部品に要求される高い伸び性と高い耐性とを有し、さらに、伸び異方性が小さくプレス加工に優れるため、自動車の外装部品等に好適に使用することができる。
<Auto parts>
The Al—Si—Mg-based aluminum alloy sheet of the present invention has a yield strength of 100 MPa or more, an elongation of 20% or more, has high extensibility and high resistance required for automotive parts, and is anisotropic in elongation. Since it has low properties and is excellent in press working, it can be suitably used for exterior parts of automobiles.
以下、本発明を実施例により詳細に説明するが、本発明は下記実施例に限定されるものではない。 EXAMPLES Hereinafter, although an Example demonstrates this invention in detail, this invention is not limited to the following Example.
＜鋳造板の作製＞
縦型の双ロール式連続鋳造装置を用いて、およそ１０００℃／秒の冷却速度で溶湯を凝固させ、最終板厚が約１ｍｍになるように圧下率に応じて厚さ１〜９ｍｍの下記表１に示す金属組成の鋳造板を得た。
具体的には、成分組成が調節された、液相線温度＋２０℃のアルミニウム合金溶湯を１ｍ／秒で回転する一対の銅製の双ロール間に、耐火性の給湯ノズルを用いて注湯し、冷却速度１０００℃／秒で凝固させて鋳造板を作製した。
［鋳造板Ａ〜Ｋ］の組成及び板厚を表１に示す。
<Production of cast plate>
Using a vertical twin-roll type continuous casting apparatus, the molten metal is solidified at a cooling rate of about 1000 ° C./second, and the following table having a thickness of 1 to 9 mm according to the reduction ratio so that the final plate thickness is about 1 mm. A cast plate having a metal composition shown in No. 1 was obtained.
Specifically, a molten aluminum alloy with a liquidus temperature of + 20 ° C., whose component composition is adjusted, is poured between a pair of copper twin rolls rotating at 1 m / second using a fire-resistant hot water supply nozzle, A cast plate was produced by solidifying at a cooling rate of 1000 ° C./second.
Table 1 shows the composition and thickness of [casted plates A to K].
［実施例１］
［鋳造板Ａ］を、圧下率７５％で冷間圧延し、５２０℃で１時間焼鈍した後、水中で急冷して［合金板１］を作製した。
[Example 1]
[Cast plate A] was cold-rolled at a reduction rate of 75%, annealed at 520 ° C. for 1 hour, and then quenched in water to produce [Alloy plate 1].
［実施例２］
［鋳造板Ｂ］を、圧下率８１％で冷間圧延する他は実施例１と同様にして［合金板２］を作製した。
[Example 2]
[Alloy plate 2] was produced in the same manner as in Example 1 except that [Cast plate B] was cold-rolled at a reduction rate of 81%.
［実施例３］
［鋳造板Ｃ］を、圧下率５０％で冷間圧延し、５３０℃で１時間焼鈍した後、水中で急冷し、さらに、合計圧下率６１％で冷間圧延する他は実施例１と同様にして［合金板３］を作製した。
[Example 3]
[Cast Sheet C] was cold-rolled at a reduction ratio of 50%, annealed at 530 ° C. for 1 hour, quenched in water, and cold-rolled at a total reduction ratio of 61%. Thus, [Alloy plate 3] was produced.
［実施例４］
［鋳造板Ｄ］を、圧下率５３％で冷間圧延し、５３０℃で１時間焼鈍した後、放冷し、さらに、合計圧下率７５％で冷間圧延する他は実施例１と同様にして［合金板４］を作製した。
[Example 4]
[Cast Plate D] was cold-rolled at a reduction ratio of 53%, annealed at 530 ° C. for 1 hour, allowed to cool, and then cold-rolled at a total reduction ratio of 75%, as in Example 1. Thus, [Alloy plate 4] was produced.
［実施例５］
［鋳造板Ｅ］を、圧下率４８％で冷間圧延し、５３５℃で１時間焼鈍した後、放冷し、さらに、合計圧下率６２％で冷間圧延する他は実施例１と同様にして［合金板５］を作製した。
[Example 5]
[Cast E] was cold-rolled at a reduction ratio of 48%, annealed at 535 ° C. for 1 hour, allowed to cool, and then cold-rolled at a total reduction ratio of 62%, as in Example 1. Thus, [Alloy plate 5] was produced.
［実施例６］
［鋳造板Ｆ］を、圧下率５８％で冷間圧延し、５３５℃で１時間焼鈍した後、放冷し、さらに、合計圧下率８５％で冷間圧延する他は実施例１と同様にして［合金板６］を作製した。
[Example 6]
[Cast Sheet F] was cold-rolled at a reduction rate of 58%, annealed at 535 ° C. for 1 hour, allowed to cool, and then cold-rolled at a total reduction rate of 85%, as in Example 1. Thus, [Alloy plate 6] was produced.
［実施例７］
［鋳造板Ｇ］を、圧下率８９％で冷間圧延する他は実施例１と同様にして［合金板７］を作製した。
[Example 7]
[Alloy plate 7] was produced in the same manner as in Example 1 except that the [cast plate G] was cold-rolled at a reduction rate of 89%.
［比較例１］
［鋳造板Ａ］を、圧下率５０％で冷間圧延し、５００℃で１時間焼鈍した後、水中で急冷して［合金板８］を作製した。
[Comparative Example 1]
[Casted plate A] was cold-rolled at a reduction rate of 50%, annealed at 500 ° C. for 1 hour, and then quenched in water to produce [Alloy plate 8].
［比較例２］
［鋳造板Ａ］を、圧下率３０％で冷間圧延し、５００℃で１時間焼鈍した後、水中で急冷して［合金板９］を作製した。
[Comparative Example 2]
[Casted plate A] was cold-rolled at a reduction rate of 30%, annealed at 500 ° C. for 1 hour, and then quenched in water to produce [Alloy plate 9].
［比較例３］
［鋳造板Ａ］を、圧下率１２％で冷間圧延し、５００℃で１時間焼鈍した後、水中で急冷して［合金板１０］を作製した。
[Comparative Example 3]
[Cast plate A] was cold-rolled at a reduction rate of 12%, annealed at 500 ° C. for 1 hour, and then quenched in water to produce [Alloy plate 10].
［比較例４］
［鋳造板Ａ］を、圧延せずに、５００℃で１時間焼鈍した後、水中で急冷して［合金板１１］を作製した。
[Comparative Example 4]
[Casted plate A] was annealed at 500 ° C. for 1 hour without rolling, and then quenched in water to produce [Alloy plate 11].
［比較例５］
［鋳造板Ｂ］を、圧下率８１％で冷間圧延し、５２０℃で１時間焼鈍した後、炉内で徐冷して［合金板１２］を作製した。
[Comparative Example 5]
[Cast plate B] was cold-rolled at a reduction rate of 81%, annealed at 520 ° C. for 1 hour, and then slowly cooled in a furnace to produce [Alloy plate 12].
［比較例６］
［鋳造板Ｈ］を、圧下率５１％で冷間圧延し、５２０℃で１時間焼鈍した後、放冷し、さらに、合計圧下率７４％で冷間圧延した後、炉内で徐冷して［合金板１３］を作製した。
[Comparative Example 6]
[Cast Sheet H] was cold-rolled at a reduction ratio of 51%, annealed at 520 ° C. for 1 hour, allowed to cool, and further cold-rolled at a total reduction ratio of 74% and then gradually cooled in the furnace. Thus, [Alloy plate 13] was produced.
［比較例７］
［鋳造板Ｉ］を、圧下率３０％で冷間圧延し、５２０℃で１時間焼鈍した後、放冷し、さらに、合計圧下率６２％で冷間圧延した後、水中で急冷して［合金板１４］を作製した。
[Comparative Example 7]
[Casted plate I] was cold-rolled at a reduction rate of 30%, annealed at 520 ° C. for 1 hour, allowed to cool, then cold-rolled at a total reduction rate of 62%, and then rapidly cooled in water. Alloy plate 14] was produced.
［比較例８］
［鋳造板Ｊ］を、圧下率７３％で冷間圧延し、５２０℃で１時間焼鈍した後、水中で急冷して［合金板１５］を作製した。
[Comparative Example 8]
[Cast plate J] was cold-rolled at a reduction ratio of 73%, annealed at 520 ° C. for 1 hour, and then quenched in water to produce [Alloy plate 15].
＜評価＞
上記合金板１〜１５を評価した。
室温での引張試験により、合金板の圧延方向と圧延直交方向の０．２％耐力、伸びを測定した。評価結果を表２に示す。
<Evaluation>
The
A 0.2% proof stress and elongation in the rolling direction and the orthogonal direction of rolling of the alloy plate were measured by a tensile test at room temperature. The evaluation results are shown in Table 2.
表２から、縦型双ロールキャスト式による連続鋳造法により製造された微細な金属組織を有する鋳造板を、高い圧下率で冷間圧延して本発明の金属組織としたＡｌ−Ｓｉ−Ｍｇ系アルミニウム合金板は、圧延方向（ＲＤ）と圧延直角方向（ＴＤ）の伸び比（ＲＤ／ＴＤ）が、０．８以上１．２以下であり、かつ伸び率が２０％以上であることがわかる。 From Table 2, an Al-Si-Mg system obtained by cold rolling a cast plate having a fine metal structure manufactured by a continuous casting method using a vertical twin roll cast method at a high reduction rate to obtain a metal structure of the present invention. The aluminum alloy sheet has an elongation ratio (RD / TD) in the rolling direction (RD) and the direction perpendicular to the rolling direction (TD) of 0.8 or more and 1.2 or less, and the elongation is 20% or more. .
実施例１と比較例８の比較から、圧下率７５％以上で圧延することで、伸び異方性が低減され高い伸び率を示すことがわかる。 From comparison between Example 1 and Comparative Example 8, it can be seen that rolling anisotropy is reduced by rolling at a rolling reduction of 75% or more, and a high elongation is exhibited.
また、比較例８と実施例３，５の比較から、合計圧下率が小さくても中間焼鈍を行うことでＳｉ粒子が丸くなってその外形が小さく、粒子間距離が拡がってセル面積の変動係数が小さくなり、等方性の伸びを示すことがわかる。 Further, from the comparison between Comparative Example 8 and Examples 3 and 5, even if the total rolling reduction is small, by performing the intermediate annealing, the Si particles are rounded, the outer shape is small, the inter-particle distance is increased, and the coefficient of variation of the cell area It can be seen that becomes smaller and shows isotropic elongation.
比較例５、６は、焼鈍後に徐冷したため、過飽和固溶体が形成されずに耐力が低下した。 Since Comparative Examples 5 and 6 were gradually cooled after annealing, the supersaturated solid solution was not formed and the yield strength was lowered.
１ Ａｌ−Ｓｉ−Ｍｇ系アルミニウム合金板
２ Ｓｉ粒子
３ 鋳造板
４ アルミニウム合金溶湯
DESCRIPTION OF
Claims (5)
４質量％以上７質量％以下のケイ素（Ｓｉ）と、
０．３質量％以上０．８質量％以下のマグネシウム（Ｍｇ）と、を含有し、
残部が、０．６質量％以下の鉄（Ｆｅ）と不可避不純物とから成り、
Ｓｉ粒子の平均最大長が２．０μｍ以下であり、
上記Ｓｉ粒子を母点としてボロノイ分割したセルの平均面積が２６μｍ２以下、かつ上記セルの面積の変動係数が０．９以下である金属組織を有し、
耐力が１００ＭＰａ以上であることを特徴とするＡｌ−Ｓｉ−Ｍｇ系アルミニウム合金板。 The main component is aluminum (Al),
4 mass% or more and 7 mass% or less of silicon (Si),
Containing 0.3 mass% or more and 0.8 mass% or less of magnesium (Mg),
The balance consists of 0.6 mass% or less of iron (Fe) and inevitable impurities,
The average maximum length of the Si particles is 2.0 μm or less,
An average area of cells obtained by Voronoi division using the Si particles as a base point is 26 μm 2 or less, and a coefficient of variation of the cell area variation coefficient is 0.9 or less,
An Al—Si—Mg-based aluminum alloy plate characterized by having a yield strength of 100 MPa or more.
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| IT202200011183A1 (en) * | 2022-05-27 | 2023-11-27 | Ferrari Spa | RECYCLED ALUMINUM FRAME FOR A ROAD VEHICLE AND CORRESPONDING PRODUCTION METHOD |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2003213356A (en) * | 2002-01-28 | 2003-07-30 | Nippon Steel Corp | High lubrication aluminum alloy sheet for bulging and production method therefor |
| JP2003321723A (en) * | 2002-02-28 | 2003-11-14 | Toyota Motor Corp | Aluminum alloy sheet with excellent bendability |
| JP2004292885A (en) * | 2003-03-26 | 2004-10-21 | Aisin Keikinzoku Co Ltd | Aluminum alloy casting material having excellent mechanical property |
| JP2010280980A (en) * | 2009-06-08 | 2010-12-16 | Daido Metal Co Ltd | Al-BASE SLIDING ALLOY AND CASTING DEVICE THEREFOR |
| JP2016084501A (en) * | 2014-10-24 | 2016-05-19 | 日産自動車株式会社 | Aluminum alloy sheet excellent in formability |
| JP2017031471A (en) * | 2015-07-31 | 2017-02-09 | 日産自動車株式会社 | Al-Si-Mg-BASED ALUMINUM ALLOY SHEET, MANUFACTURING METHOD OF THE ALLOY SHEET AND AUTOMOBILE COMPONENT USING ALLOY SHEET |
-
2018
- 2018-04-24 JP JP2018083140A patent/JP7378916B2/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2003213356A (en) * | 2002-01-28 | 2003-07-30 | Nippon Steel Corp | High lubrication aluminum alloy sheet for bulging and production method therefor |
| JP2003321723A (en) * | 2002-02-28 | 2003-11-14 | Toyota Motor Corp | Aluminum alloy sheet with excellent bendability |
| JP2004292885A (en) * | 2003-03-26 | 2004-10-21 | Aisin Keikinzoku Co Ltd | Aluminum alloy casting material having excellent mechanical property |
| JP2010280980A (en) * | 2009-06-08 | 2010-12-16 | Daido Metal Co Ltd | Al-BASE SLIDING ALLOY AND CASTING DEVICE THEREFOR |
| JP2016084501A (en) * | 2014-10-24 | 2016-05-19 | 日産自動車株式会社 | Aluminum alloy sheet excellent in formability |
| JP2017031471A (en) * | 2015-07-31 | 2017-02-09 | 日産自動車株式会社 | Al-Si-Mg-BASED ALUMINUM ALLOY SHEET, MANUFACTURING METHOD OF THE ALLOY SHEET AND AUTOMOBILE COMPONENT USING ALLOY SHEET |
Non-Patent Citations (1)
| Title |
|---|
| アルミニウムハンドブック（第８版）, JPN6019017970, 15 February 2017 (2017-02-15), JP, pages 255 - 262, ISSN: 0004919019 * |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| IT202200011183A1 (en) * | 2022-05-27 | 2023-11-27 | Ferrari Spa | RECYCLED ALUMINUM FRAME FOR A ROAD VEHICLE AND CORRESPONDING PRODUCTION METHOD |
| EP4283001A1 (en) | 2022-05-27 | 2023-11-29 | FERRARI S.p.A. | Recycled aluminium frame for a road vehicle and corresponding production method |
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