JP2015010259A - Aluminum alloy sheet - Google Patents
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本発明は、アルミニウム合金板に関する。より詳しくは、Ａｌ−Ｓｉ−Ｍｇ系のアルミニウム合金板に関する。 The present invention relates to an aluminum alloy plate. More specifically, the present invention relates to an Al—Si—Mg based aluminum alloy plate.
近年、地球環境などへの配慮から、自動車等の車両の軽量化の社会的要求はますます高まってきている。かかる要求に答えるべく、自動車パネル、特にフード、ドア、ルーフなどの大型ボディパネル（アウタパネル、インナパネル）の材料として、鋼板等の鉄鋼材料にかえて、成形性や塗装焼付硬化特性に優れた、より軽量なアルミニウム合金材の適用が増加しつつある。 In recent years, due to consideration for the global environment and the like, social demands for weight reduction of vehicles such as automobiles are increasing. In order to respond to such demands, as a material for large body panels (outer panels, inner panels) such as automobile panels, especially hoods, doors, roofs, etc., instead of steel materials such as steel plates, it was excellent in formability and paint bake hardening properties. The application of lighter aluminum alloy materials is increasing.
このアルミニウム合金材として、Ａｌ−Ｍｇ−Ｓｉ系のＡＡ乃至ＪＩＳ規格の６０００系（以下、単に６０００系とも記す）アルミニウム合金板が多く使用されている。 As the aluminum alloy material, Al-Mg-Si-based AA to JIS standard 6000 series (hereinafter also simply referred to as 6000 series) aluminum alloy plates are often used.
この６０００系（Ａｌ−Ｍｇ−Ｓｉ系）アルミニウム合金板は、前記パネルへのプレス成形後のパネルの塗装焼付処理により硬化して、強度（硬度）が向上し、パネルとしての必要な強度を確保できる、優れた塗装焼付硬化特性がある。以下、この塗装焼付硬化特性をベークハード性あるいはＢＨ性ともいう。 This 6000 series (Al-Mg-Si) aluminum alloy sheet is hardened by the paint baking process of the panel after press molding to the panel, and the strength (hardness) is improved, ensuring the necessary strength as a panel. It has excellent paint bake-hardening properties. Hereinafter, this paint bake hardening property is also referred to as bake hard property or BH property.
従来から、このような６０００系アルミニウム合金板の塗装焼付硬化特性の向上に関して、Ｍｇ−Ｓｉ系クラスタを制御することが種々提案されている。このクラスタ制御につき、最近では、これらＭｇ−Ｓｉ系クラスタを、６０００系アルミニウム合金板の示差走査熱分析（以下、「ＤＳＣ」ともいう。）曲線の吸熱ピークや発熱ピークにて測定した上で制御する技術が提案されている。 Conventionally, various proposals have been made to control Mg—Si clusters for improving the bake hardening characteristics of such 6000 series aluminum alloy plates. With regard to this cluster control, recently, these Mg-Si based clusters are controlled after being measured at an endothermic peak or an exothermic peak of a differential scanning calorimetry (hereinafter also referred to as “DSC”) curve of a 6000 series aluminum alloy plate. Techniques to do this have been proposed.
例えば、特許文献１及び２では、低温での時効硬化能を阻害している要因として、これらＭｇ−Ｓｉ系クラスタ、特に、Ｓｉ／空孔クラスタ（ＧＰI）の生成量を規制することが提案されている。特許文献１には、室温時効抑制と低温時効硬化能を阻害するＧＰIの生成量を規制するために、Ｔ４材（溶体化処理後自然時効後）のＤＳＣにおいて、ＧＰIの溶解に相当する１５０〜２５０℃の温度範囲における吸熱ピークがないことを規定している。また、特許文献１では、このＧＰIの生成を抑制乃至制御するために、溶体化及び室温まで焼入れ処理した後に、７０〜１５０℃で０．５〜５０時間程度保持する低温熱処理を施している。 For example, in Patent Documents 1 and 2, it is proposed to regulate the amount of these Mg-Si-based clusters, particularly Si / vacancy clusters (GPI), as a factor inhibiting the age-hardening ability at low temperatures. ing. In Patent Document 1, in order to regulate the production amount of GPI that inhibits room temperature aging suppression and low-temperature age-hardening ability, in DSC of T4 material (after solution aging and after natural aging), 150- It defines that there is no endothermic peak in the temperature range of 250 ° C. Moreover, in patent document 1, in order to suppress thru | or control this production | generation of GPI, after performing solution treatment and quenching to room temperature, the low temperature heat processing hold | maintained at 70-150 degreeC for about 0.5 to 50 hours is performed.
また、特許文献３では、低温での時効硬化能を得るため、過剰Ｓｉ型の６０００系アルミニウム合金材の溶体化および焼入れ処理を含む調質処理後のＤＳＣ曲線において、Ｓｉ／空孔クラスタ（ＧＰI）の溶解に相当する１５０〜２５０℃の温度範囲におけるマイナスの吸熱ピーク高さと、Ｍｇ／Ｓｉクラスタ（ＧＰII）の析出に相当する２５０〜３００℃の温度範囲におけるプラスの発熱ピーク高さとを制御している。 Further, in Patent Document 3, in order to obtain age hardening ability at a low temperature, in a DSC curve after tempering treatment including solution treatment and quenching treatment of excess Si type 6000 series aluminum alloy material, Si / vacancy cluster (GPI ) To control the negative endothermic peak height in the temperature range of 150 to 250 ° C. corresponding to the dissolution of) and the positive exothermic peak height in the temperature range of 250 to 300 ° C. corresponding to the precipitation of Mg / Si clusters (GPII). ing.
特許文献４では、低温での時効硬化能を得るため、６０００系アルミニウム合金板の調質処理後のＤＳＣ曲線において、１００〜２００℃の温度範囲における発熱ピーク高さＷ１を５０μＷ以上とし、かつ、２００〜３００℃の温度範囲における発熱ピーク高さＷ２と前記Ｗ１との比Ｗ２／Ｗ１を２０．０以下としている。ここで、前記発熱ピークＷ１は、人工時効硬化処理時のβ”相（Ｍｇ２Ｓｉ相）の核生成サイトとなるＧＰゾーンの析出に対応しており、Ｗ１のピーク高さが高いほど、人工時効硬化処理の際のβ”の核生成サイトとなるＧＰゾーンが、調質処理後の板に予め形成、確保されているとする。一方、発熱ピークＷ２の方は、β”相自体の析出ピークに対応しており、プレス成形される板を予め低耐力化させて成形性を確保するために、この発熱ピークＷ２の高さを小さくするとしている。 In Patent Document 4, to obtain the age hardening ability at low temperature, and in the DSC curve after refining of 6000 series aluminum alloy sheet, the exothermic peak heights W 1 in the temperature range of 100 to 200 ° C. 50 W or higher, and The ratio W 2 / W 1 between the exothermic peak height W 2 and the W 1 in the temperature range of 200 to 300 ° C. is 20.0 or less. Here, the exothermic peak W 1 corresponds to the precipitation of the GP zone that becomes the nucleation site of the β ″ phase (Mg 2 Si phase) during the artificial age hardening treatment, and the higher the peak height of W 1 is, It is assumed that a GP zone that becomes a nucleation site of β ″ at the time of artificial age hardening is formed and secured in advance on the plate after the tempering treatment. On the other hand, the exothermic peak W 2 corresponds to the precipitation peak of the β ″ phase itself, and the exothermic peak W 2 has a higher exothermic peak W 2 in order to ensure the formability by reducing the yield strength of the press-formed plate in advance. The size is supposed to be small.
しかしながら、前述の従来技術であっても、室温で時効硬化しやすく、かつ室温時効時間などの条件が種々異なるようなＡｌ―Ｓｉ―Ｍｇ系のアルミニウム合金板を、加熱温度が１５０℃又は１３５℃などの低温の塗装焼付硬化処理で、安定して高強度（高硬度）とすることは難しいという実情がある。 However, even with the above-described prior art, an Al—Si—Mg-based aluminum alloy plate that is easy to age harden at room temperature and has various conditions such as room temperature aging time, has a heating temperature of 150 ° C. or 135 ° C. There is a fact that it is difficult to stably achieve high strength (high hardness) by low-temperature paint baking and curing treatment.
本発明は、前述の実情に鑑みてなされたものであり、低温の塗装焼付硬化処理であっても、安定した高強度が得られるＡｌ―Ｓｉ―Ｍｇ系のアルミニウム合金板を提供することを主目的とする。 The present invention has been made in view of the above circumstances, and mainly provides an Al—Si—Mg-based aluminum alloy plate that can obtain a stable high strength even by low-temperature paint baking and hardening treatment. Objective.
すなわち、本発明は、Ｍｇ：０.２〜２.０質量％、Ｓｉ：０.３〜２.０質量％、Ｆｅ：０．５質量％以下、Ｌｉ：０．００５〜０．１質量％を含み、残部がＡｌ及び不可避的不純物からなるアルミニウム合金板を提供する。 That is, the present invention is Mg: 0.2-2.0 mass%, Si: 0.3-2.0 mass%, Fe: 0.5 mass% or less, Li: 0.005-0.1 mass% And an aluminum alloy plate with the balance being Al and inevitable impurities.
本発明によれば、低温の塗装焼付硬化処理であっても、安定して高強度が得られるＡｌ―Ｓｉ―Ｍｇ系のアルミニウム合金板を得ることができる。 According to the present invention, it is possible to obtain an Al—Si—Mg-based aluminum alloy plate that can stably obtain high strength even by low-temperature paint bake hardening treatment.
以下、本発明を実施するための形態について、詳細に説明する。なお、本発明は、以下に説明する実施形態に限定されるものではない。
また、本発明でいう「アルミニウム合金板」とは、冷間圧延後、調質処理を施した後の板（圧延板）をいう。
Hereinafter, embodiments for carrying out the present invention will be described in detail. Note that the present invention is not limited to the embodiments described below.
Further, the “aluminum alloy plate” in the present invention refers to a plate (rolled plate) after cold rolling and after tempering treatment.
アルミニウム合金板の化学成分組成：
先ず、本発明の実施形態に係る６０００系アルミニウム合金板の化学成分組成について、説明する。
Chemical composition of aluminum alloy sheet:
First, the chemical component composition of the 6000 series aluminum alloy plate according to the embodiment of the present invention will be described.
対象とする６０００系のアルミニウム合金板は、自動車パネルに成形された後の、塗装焼付処理などの例えば１３５℃〜１７０℃の比較的低温の人工時効処理時の加熱により時効硬化し、必要な強度（硬度）を確保できる優れた時効硬化能（ＢＨ性）を有していることが要求される。
また、前記した自動車の外板用の板などとして、優れた成形性及び溶接性、又は耐食性などの諸特性もあわせて要求される。
The target 6000 series aluminum alloy plate is age-hardened by heating at a relatively low temperature artificial aging treatment of, for example, 135 ° C. to 170 ° C. after being molded into an automobile panel, for example, paint baking treatment, and required strength It is required to have excellent age-hardening ability (BH property) that can ensure (hardness).
In addition, various properties such as excellent formability and weldability, and corrosion resistance are also required for the above-described automobile outer plate.
このような要求特性を満足するため、本実施形態に係るアルミニウム合金板では、Ｍｇ：０．２〜２．０質量％、Ｓｉ：０．３〜２．０質量％、Ｆｅ：０．５質量％以下、及びＬｉ：０．００５〜０．１質量％を各々含み、残部がＡｌ及び不可避的不純物からなるものと規定する。 In order to satisfy such required characteristics, in the aluminum alloy plate according to the present embodiment, Mg: 0.2 to 2.0 mass%, Si: 0.3 to 2.0 mass%, Fe: 0.5 mass% % And Li: 0.005 to 0.1 mass%, respectively, and the balance is defined as consisting of Al and inevitable impurities.
これらＭｇ、Ｓｉ、Ｆｅ及びＬｉ以外の、Ｍｎ、Ｃｕ、Ｃｒ、Ｔｉ、及びＺｎなどのその他の元素は、本実施形態のアルミニウム合金板のＬｉ含有による効果を発揮させるために、いずれも０．０２質量％以下の含有量（許容量）とする。 Other than these Mg, Si, Fe, and Li, other elements such as Mn, Cu, Cr, Ti, and Zn all have an O.O. The content (allowable amount) is 02% by mass or less.
上記各元素の含有量範囲と意義又は許容量について以下に説明する。 The content range and significance or allowable amount of each element will be described below.
［Ｓｉ：０．３〜２.０質量％］
ＳｉはＭｇとともに、本実施形態のアルミニウム合金板において、塗装焼付処理などの、例えば１３５℃〜１７０℃の低温での人工時効処理時に、ＢＨ性に効く時効析出物であるβ”相の析出量を満足し、時効硬化能を高めるために必須の元素である。また、固溶強化や、プレス成形性に影響する全伸びを向上させる効果もある。
[Si: 0.3 to 2.0% by mass]
Si, together with Mg, in the aluminum alloy plate of the present embodiment, during the artificial aging treatment at a low temperature of, for example, 135 ° C. to 170 ° C., such as paint baking treatment, the amount of precipitation of β ″ phase, which is an aging precipitate that works on BH properties In addition, it is an essential element for enhancing age-hardening ability, and also has the effect of improving solid solution strengthening and total elongation that affects press formability.
しかしながら、Ｓｉ含有量が０．３質量％未満の場合、Ｓｉの絶対量が不足するため、前記β”相の析出量が不足して、ＢＨ性が著しく低下する可能性がある。更には、全伸びなどの機械的特性も兼備することが難しくなる。
一方、Ｓｉ含有量が２．０質量％を超えると、粗大な晶出物及び析出物が形成されて、曲げ加工性や全伸びなどが著しく低下するおそれがある。更に、溶接性も著しく阻害されるおそれがある。
よって、本実施形態のアルミニウム合金板では、Ｓｉの含有量を０．３〜２．０質量％、好ましくは０.５〜１.２質量％とする。
However, when the Si content is less than 0.3% by mass, the absolute amount of Si is insufficient, so that the precipitation amount of the β ″ phase is insufficient, and the BH property may be significantly lowered. It becomes difficult to combine mechanical properties such as total elongation.
On the other hand, when the Si content exceeds 2.0% by mass, coarse crystallized products and precipitates are formed, and bending workability, total elongation, and the like may be significantly reduced. Furthermore, weldability may be significantly impaired.
Therefore, in the aluminum alloy plate of the present embodiment, the Si content is set to 0.3 to 2.0 mass%, preferably 0.5 to 1.2 mass%.
［Ｍｇ：０．２〜２．０質量％］
Ｍｇは、Ｓｉとともに塗装焼付処理などの前記低温での人工時効処理時に、ＢＨ性に効く時効析出物であるβ”相の析出により、時効硬化能を高めるために必須の元素である。また、固溶強化や、プレス成形性に影響する全伸びを向上させる効果もある。
[Mg: 0.2 to 2.0% by mass]
Mg is an essential element for enhancing age-hardening ability by precipitation of β ″ phase, which is an aging precipitate effective for BH properties, at the time of artificial aging treatment at low temperatures such as paint baking treatment together with Si. There is also an effect of improving solid solution strengthening and total elongation that affects press formability.
しかしながら、Ｍｇ含有量が０．２質量％未満の場合、Ｍｇの絶対量が不足するため、前記β”相の析出量が不足して、ＢＨ性が著しく低下する可能性がある。更には、全伸びなどの機械的特性も兼備することが難しくなる。
一方、Ｍｇ含有量が２．０質量％を超えると、粗大な晶出物及び析出物が形成されて、曲げ加工性や全伸びなどが著しく低下するおそれがある。更に、溶接性も著しく阻害されるおそれがある。
よって、本実施形態のアルミニウム合金板では、Ｍｇの含有量を０．２〜２．０質量％とし、好ましくは０.３〜１.０質量％とする。
However, when the Mg content is less than 0.2% by mass, the absolute amount of Mg is insufficient, so that the precipitation amount of the β ″ phase is insufficient, and the BH property may be significantly lowered. It becomes difficult to combine mechanical properties such as total elongation.
On the other hand, when the Mg content exceeds 2.0% by mass, coarse crystallized substances and precipitates are formed, and there is a possibility that bending workability, total elongation, and the like are remarkably reduced. Furthermore, weldability may be significantly impaired.
Therefore, in the aluminum alloy plate of this embodiment, the Mg content is 0.2 to 2.0 mass%, preferably 0.3 to 1.0 mass%.
［Ｆｅ：０．５質量％以下］
アルミニウム合金板のリサイクルの観点から、溶解原料として、高純度アルミニウム地金だけではなく、Ａｌ合金スクラップ材、低純度アルミニウム地金などを溶解原料として使用した場合には、Ｆｅの混入量（含有量）が必然的に多くなる。ただし、ＦｅはＡｌとの金属間化合物を形成するため、Ｆｅの含有量が０．５質量％までであれば、本実施形態のアルミニウム合金板におけるＬｉ含有による効果発現に対して悪影響を及ぼさない。
したがって、本実施形態のアルミニウム合金板では、Ｆｅの含有量を０．５質量％以下とし、好ましくは０.３質量％以下とする。
[Fe: 0.5% by mass or less]
From the viewpoint of recycling aluminum alloy sheets, not only high-purity aluminum bullion but also aluminum alloy scrap material, low-purity aluminum bullion, etc. are used as melting raw materials. ) Will inevitably increase. However, since Fe forms an intermetallic compound with Al, as long as the Fe content is up to 0.5% by mass, it does not adversely affect the effects of the Li content in the aluminum alloy plate of this embodiment. .
Therefore, in the aluminum alloy plate of the present embodiment, the Fe content is 0.5 mass% or less, preferably 0.3 mass% or less.
［Ｌｉ：０．００５〜０．１質量％］
Ｌｉは、塗装焼付処理などの前記低温での人工時効処理時に、ＢＨ性に効くβ”相の析出を促進して、このβ”相の析出量を増加させる。この点で、Ｌｉは時効硬化能を高めるために必須の元素である。
[Li: 0.005 to 0.1% by mass]
Li promotes the precipitation of the β ″ phase effective for the BH property during the artificial aging treatment at a low temperature such as the paint baking treatment, and increases the precipitation amount of the β ″ phase. In this respect, Li is an essential element for enhancing age hardening ability.
Ｌｉ含有量が０．００５質量％未満の場合、Ｌｉの絶対量が不足するため、前記β”相の析出量が不足して、ＢＨ性が著しく低下する可能性がある。
一方、Ｌｉは、溶解、鋳造時に鋳塊に含有させること自体が難しく、多く含有させることができない。また、Ｌｉ含有量が０．１質量％を超えると、成形性や全伸びなどが著しく低下するおそれがある。
よって、本実施形態のアルミニウム合金板では、Ｌｉの含有量を０．００５〜０.１質量％とし、好ましくは０.０２〜０.１質量％とする。
When the Li content is less than 0.005% by mass, the absolute amount of Li is insufficient, so that the precipitation amount of the β ″ phase is insufficient, and the BH property may be significantly lowered.
On the other hand, Li is difficult to be contained in the ingot at the time of melting and casting, and cannot be contained in a large amount. On the other hand, if the Li content exceeds 0.1% by mass, the moldability, total elongation, and the like may be significantly reduced.
Therefore, in the aluminum alloy plate of the present embodiment, the Li content is set to 0.005 to 0.1% by mass, preferably 0.02 to 0.1% by mass.
なお、６０００系アルミニウム合金板の分野において、特開平１１−７１６２３号公報では、自動車ボディパネル用として、プレス成形性、耐食性、塗装焼付後の強度向上を目的として、鋳造時に生じる晶出物を微細分散させたり球状化させるために、Ｎａ、Ｓｒ、Ｓｂ、Ｃａ、Ｔｅ、Ｂａ、Ｌｉ、Ｋ、Ｂｉ、Ｐ、Ａｓ、及びＳｅの元素のうち１種以上を添加することが開示されている。このように、この特許文献では、鋳造時に生じる晶出物を微細分散又は球状化させるための添加元素として、Ｌｉが使用され得ることが記載されているが、Ｌｉに特化されているわけではない。 In the field of 6000 series aluminum alloy plates, Japanese Patent Application Laid-Open No. 11-71623 discloses finely crystallized products produced during casting for the purpose of improving the press formability, corrosion resistance, and strength after paint baking for automobile body panels. It is disclosed that at least one of the elements Na, Sr, Sb, Ca, Te, Ba, Li, K, Bi, P, As, and Se is added for dispersion or spheroidization. As described above, in this patent document, it is described that Li can be used as an additive element for finely dispersing or spheroidizing the crystallized product generated at the time of casting, but it is not specialized in Li. Absent.
本実施形態のアルミニウム合金板のように、前述の元素のうちのＬｉだけの特異な効果である、低温での塗装焼付処理時にＢＨ性に効く時効析出物であるβ”相の析出を促進させる効果については、従来技術では、認識も示唆もされていなかった。 Like the aluminum alloy plate of the present embodiment, it promotes the precipitation of the β ″ phase, which is an aging precipitate that is effective for BH at the time of coating baking at low temperature, which is a unique effect of only Li among the aforementioned elements. The effect was neither recognized nor suggested in the prior art.
また、前述の特開平１１−７１６２３号公報では、上述の通り、Ｌｉを添加できるものの、その実施例においても、板の製法は冷延板後に焼鈍して製造したことが記載されているだけである。つまり、この特許文献には、焼鈍（調質処理）が、溶体化、焼入れ処理であるか単なる焼鈍であるかや、その温度条件など、具体的な条件は記載されていない。したがって、この特許文献では、本実施形態に係るアルミニウム合金板で規定するようなβ”相の析出物が存在する組織となっているか否かは全く不明であり、むしろ、そのような組織になってはいない蓋然性の方が高い。 In addition, in the above-mentioned Japanese Patent Application Laid-Open No. 11-71623, as described above, Li can be added, but also in the examples, the manufacturing method of the plate is only described as being manufactured by annealing after cold rolling. is there. That is, this patent document does not describe specific conditions such as whether the annealing (tempering treatment) is a solution treatment, a quenching treatment, or a simple annealing, and temperature conditions thereof. Therefore, in this patent document, it is completely unknown whether or not a β ″ phase precipitate exists as defined by the aluminum alloy plate according to the present embodiment. There is a higher probability of not.
［残部：Ａｌ及び不可避的不純物］
前述したＭｇ、Ｓｉ、Ｆｅ及びＬｉの各成分以外の成分、すなわち残部は、Ａｌ及び不可避的不純物である。本実施形態のアルミニウム合金板では特に、そのアルミニウム合金板におけるＬｉ含有による効果を発揮させるために、不可避的不純物はいずれも０．０２質量％以下の含有量（許容量）に規制する。不可避的不純物としては、例えば、Ｍｎ、Ｃｕ、Ｃｒ、Ｔｉ、Ｚｎなどが挙げられる。
[Balance: Al and inevitable impurities]
Components other than the above-described components of Mg, Si, Fe, and Li, that is, the balance, are Al and inevitable impurities. In particular, in the aluminum alloy plate of the present embodiment, inevitable impurities are restricted to a content (allowable amount) of 0.02% by mass or less in order to exert the effect of the Li content in the aluminum alloy plate. Examples of inevitable impurities include Mn, Cu, Cr, Ti, and Zn.
製造方法：
次に、本実施形態のアルミニウム合金板の製造方法について説明する。
本実施形態のアルミニウム合金板は、上記６０００系成分組成のアルミニウム合金鋳塊を鋳造後に均質化熱処理し、熱間圧延、冷間圧延が施されて所定の板厚とされ、更に溶体化焼入れなどの調質処理が施されて製造される。
Production method:
Next, the manufacturing method of the aluminum alloy plate of this embodiment is demonstrated.
The aluminum alloy plate of this embodiment is subjected to homogenization heat treatment after casting the above-mentioned aluminum alloy ingot having the above-mentioned 6000 series composition, and is subjected to hot rolling and cold rolling to a predetermined plate thickness, and further is solution-quenched and the like The tempering treatment is applied.
（溶解、鋳造冷却速度）
先ず、溶解、鋳造工程では、上記６０００系成分組成範囲内に溶解調整されたアルミニウム合金溶湯を、連続鋳造法、半連続鋳造法（ＤＣ鋳造法）等の通常の溶解鋳造法を適宜選択して鋳造する。
(Dissolution, casting cooling rate)
First, in the melting and casting process, an ordinary molten casting method such as a continuous casting method and a semi-continuous casting method (DC casting method) is appropriately selected for the molten aluminum alloy adjusted to be dissolved within the above-mentioned 6000 series component composition range. Cast.
（均質化熱処理）
次いで、前記鋳造されたアルミニウム合金鋳塊に、熱間圧延に先立って、均質化熱処理を施す。この均質化熱処理（均熱処理）は、組織の均質化、すなわち、鋳塊組織中の結晶粒内の偏析をなくすことを目的に行われる。そのため、均質化熱処理温度は、５００℃以上でアルミニウム合金板の融点未満、均質化時間は４時間以上の範囲から適宜選択される。
(Homogenization heat treatment)
Next, the cast aluminum alloy ingot is subjected to a homogenization heat treatment prior to hot rolling. This homogenization heat treatment (soaking) is performed for the purpose of homogenizing the structure, that is, eliminating segregation in the crystal grains in the ingot structure. Therefore, the homogenization heat treatment temperature is appropriately selected from the range of 500 ° C. or higher and less than the melting point of the aluminum alloy plate, and the homogenization time of 4 hours or more.
（熱間圧延）
この均質化熱処理後の熱間圧延は、好ましくは開始温度を４００℃〜固相線温度として行う。熱延板の冷間圧延前の焼鈍（荒鈍）は必ずしも必要ではないが、成形性などの特性を更に向上させるために実施しても良い。
(Hot rolling)
The hot rolling after the homogenization heat treatment is preferably performed at a start temperature of 400 ° C. to a solidus temperature. Although annealing (roughening) of the hot-rolled sheet before cold rolling is not necessarily required, it may be performed to further improve the properties such as formability.
（冷間圧延）
冷間圧延では、上記熱延板を所望の最終板厚の冷延板に圧延する。前記荒鈍と同様の目的で、この冷間圧延のパス間で中間焼鈍を行っても良い。
(Cold rolling)
In cold rolling, the hot rolled sheet is rolled into a cold rolled sheet having a desired final sheet thickness. For the same purpose as the roughening, intermediate annealing may be performed between the cold rolling passes.
（溶体化及び焼入れ処理）
冷延板に調質処理として溶体化焼入れ処理を行う。各元素の十分な固溶量を得るためには、溶体化処理温度を５２０℃以上とすることが好ましい。保持時間はできるだけ長い方が望ましい。また、成形性を低下させる粗大な粒界化合物形成を抑制するために、焼入れ時の冷却速度はできるだけ早い方が望ましく、水冷することが好ましい。
(Solution and quenching)
A solution-quenching treatment is performed as a tempering treatment on the cold rolled sheet. In order to obtain a sufficient solid solution amount of each element, the solution treatment temperature is preferably set to 520 ° C. or higher. The holding time should be as long as possible. Moreover, in order to suppress the formation of coarse grain boundary compounds that lower the moldability, the cooling rate during quenching is desirably as fast as possible, and water cooling is preferable.
（再加熱処理）
この室温まで焼入れ冷却した後に得られた板を、必要により再加熱処理（予備時効処理）する。この再加熱処理は好ましくは７０〜１５０℃の温度域に、バッチ炉では１時間以上保持する。
(Reheating treatment)
If necessary, the plate obtained after quenching and cooling to room temperature is reheated (preliminary aging treatment). This reheating treatment is preferably performed in a temperature range of 70 to 150 ° C. for 1 hour or longer in a batch furnace.
以上述べた本実施形態のアルミニウム合金板では、６０００系アルミニウム合金にＬｉを特定範囲の量で含有する。これによって、加熱温度が例えば１３５℃〜１７０℃などの低温条件での塗装焼付硬化処理であっても、塗装焼付後の強度（硬度）を安定して高めた６０００系のアルミニウム合金板を提供することができる。このため、本実施形態のアルミニウム合金板は、例えば自動車などの輸送機の部材に適用することができる。 In the aluminum alloy plate of this embodiment described above, 6000 series aluminum alloy contains Li in a specific range. This provides a 6000 series aluminum alloy plate that stably increases the strength (hardness) after coating baking even when the heating temperature is a coating baking hardening process at a low temperature such as 135 ° C. to 170 ° C. be able to. For this reason, the aluminum alloy plate of this embodiment is applicable to the members of transport machines, such as a motor vehicle.
以下、本発明の実施例及び比較例を挙げて、本発明の効果について具体的に説明する。 Hereinafter, the effects of the present invention will be specifically described with reference to Examples and Comparative Examples of the present invention.
以下に説明する実施例及び比較例では、それぞれ６０００系アルミニウム合金板を、溶体化及び焼入れ処理後の調質（再加熱処理）条件で作り分けた。 In the examples and comparative examples described below, 6000 series aluminum alloy plates were separately prepared under the tempering (reheating treatment) conditions after solution treatment and quenching treatment.
表１に示すように、同じ合金組成同士の実施例１及び２と、同じ合金組成同士の比較例１及び２の６０００系アルミニウム合金冷延板を各々製造して、溶体化及び焼入れ処理後の調質工程をタイプＡとタイプＢとした二種類に作り分けた。
調質工程タイプＡは、溶体化及び焼入れ処理後に３０分室温保持したままのアルミニウム合金板とした。
調質工程タイプＢは、溶体化及び焼入れ処理後に１００℃×５時間の予備時効処理後に３０分室温保持させたアルミニウム合金板とした。
As shown in Table 1, 6000 series aluminum alloy cold-rolled sheets of Examples 1 and 2 having the same alloy composition and Comparative Examples 1 and 2 having the same alloy composition were produced, respectively, and after solution treatment and quenching treatment. The tempering process was divided into two types, Type A and Type B.
The tempering process type A was an aluminum alloy plate that was kept at room temperature for 30 minutes after solution treatment and quenching treatment.
The tempering process type B was an aluminum alloy plate kept at room temperature for 30 minutes after a pre-aging treatment at 100 ° C. for 5 hours after the solution treatment and quenching treatment.
アルミニウム合金冷延板の具体的な製造条件は次の通りである。
表１に示す各組成の鋳塊をＤＣ鋳造法により共通して溶製して鋳塊とした。この際、実施例１及び２はＬｉを含む同じ組成、比較例１及び２はＬｉを含まない同じ組成とした。続いて、鋳塊を、各例とも共通して、５４０℃×４時間均熱処理した後、熱延開始温度を５４０℃として熱間圧延を開始し、厚さ２．５ｍｍの熱延板とした。この熱延板を、各例とも共通して、そのまま荒焼無しで、また冷延パス途中の中間焼鈍無しで、冷間圧延を行い、厚さ１．０ｍｍの冷延板とした。
The specific production conditions for the aluminum alloy cold-rolled sheet are as follows.
Ingots having respective compositions shown in Table 1 were commonly melted by DC casting to form ingots. At this time, Examples 1 and 2 had the same composition containing Li, and Comparative Examples 1 and 2 had the same composition not containing Li. Subsequently, the ingot was subjected to a soaking treatment at 540 ° C. for 4 hours in common with each example, and then hot rolling was started at a hot rolling start temperature of 540 ° C. to obtain a hot rolled plate having a thickness of 2.5 mm. . In common with each example, this hot-rolled sheet was cold-rolled without any rough firing and without intermediate annealing in the middle of the cold-rolling pass to obtain a cold-rolled sheet having a thickness of 1.0 mm.
更に、この各冷延板を、各例とも共通して、硝石炉で５５０℃×３０分溶体化処理し、その後直ちに室温まで水冷する、溶体化焼入れ処理を行った。この後、前記タイプＡ、Ｂの二種類の調質を行った。 Furthermore, each cold-rolled sheet was subjected to a solution hardening treatment in which each of the cold-rolled plates was subjected to a solution treatment in a glass stone furnace at 550 ° C. for 30 minutes and then immediately cooled to room temperature. Thereafter, the two types of tempering, Type A and B, were performed.
これら調質後の各アルミニウム合金板から供試板（ブランク）を任意に切り出し、各供試板の組織と特性とを以下の通り測定、評価した。これらの結果も表１に示す。 A test plate (blank) was arbitrarily cut out from each tempered aluminum alloy plate, and the structure and characteristics of each test plate were measured and evaluated as follows. These results are also shown in Table 1.
（塗装焼付硬化特性）
前記供試板の塗装焼付相当の人工時効処理後の強度を調査するために、各例とも、１３５℃、１５０℃、及び１７０℃の各々異なる温度で共通して２０分間保持した。
(Paint bake-hardening properties)
In order to investigate the strength after the artificial aging treatment equivalent to the paint baking of the test plate, each example was held at different temperatures of 135 ° C., 150 ° C., and 170 ° C. for 20 minutes in common.
（ビッカース硬度）
ビッカース硬度の測定は、ビッカース硬度計（株式会社マツザワ製）にて、０.５ｋｇの荷重を加え、前記供試板表面の任意の箇所を７箇所計測して、最大値と最小値を除外した５点の値を平均化した。この測定は、１３５℃、１５０℃、及び１７０℃の各温度での人工時効処理後に行った。この結果を表１に示す。
(Vickers hardness)
Vickers hardness was measured with a Vickers hardness tester (manufactured by Matsuzawa Co., Ltd.) by applying a load of 0.5 kg, measuring seven arbitrary locations on the surface of the test plate, and excluding the maximum and minimum values. Five point values were averaged. This measurement was performed after artificial aging treatment at 135 ° C, 150 ° C, and 170 ° C. The results are shown in Table 1.
表１に示す通り、実施例１及び２は、組成としてＬｉを含むなど本発明範囲内であった。この結果、実施例１及び２のアルミニウム合金板では、１３５℃、１５０℃、及び１７０℃の各温度での人工時効処理後のビッカース硬さが、同じ調質工程タイプの比較例に比べて高いものであった。 As shown in Table 1, Examples 1 and 2 were within the scope of the present invention, including Li as a composition. As a result, in the aluminum alloy plates of Examples 1 and 2, the Vickers hardness after the artificial aging treatment at temperatures of 135 ° C., 150 ° C., and 170 ° C. is higher than that of the comparative example of the same tempering process type. It was a thing.
これに対して、比較例１及び２のアルミニウム合金板は、調質を含めて実施例と同じ条件で製造しているものの、Ｌｉを含有していない。この結果、比較例１及び２のアルミニウム合金板では、１３５℃、１５０℃、及び１７０℃の各温度での人工時効処理後のビッカース硬さが、同じ調質工程タイプの実施例に比べて劣っていた。 On the other hand, the aluminum alloy plates of Comparative Examples 1 and 2 are manufactured under the same conditions as in the Examples including the tempering, but do not contain Li. As a result, in the aluminum alloy plates of Comparative Examples 1 and 2, the Vickers hardness after the artificial aging treatment at each temperature of 135 ° C., 150 ° C., and 170 ° C. is inferior to the examples of the same tempering process type. It was.
以上の実施例の結果から、低温条件での塗装焼付相当の人工時効処理後の強度向上に対して、本発明で規定するＬｉ及び組織を満たす必要性があることが裏付けられる。 From the results of the above examples, it is confirmed that there is a need to satisfy Li and the structure defined in the present invention for the strength improvement after artificial aging treatment corresponding to paint baking under low temperature conditions.
Claims (1)
Ｓｉ：０.３〜２.０質量％、
Ｆｅ：０．５質量％以下、
Ｌｉ：０．００５〜０．１質量％を含み、
残部がＡｌ及び不可避的不純物からなるアルミニウム合金板。 Mg: 0.2 to 2.0% by mass,
Si: 0.3 to 2.0% by mass,
Fe: 0.5% by mass or less,
Li: 0.005 to 0.1% by mass,
An aluminum alloy plate with the balance being Al and inevitable impurities.
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