JP2001003128A - Impact absorbing member excellent in crushing crack resistance - Google Patents
Impact absorbing member excellent in crushing crack resistanceInfo
- Publication number
- JP2001003128A JP2001003128A JP17231999A JP17231999A JP2001003128A JP 2001003128 A JP2001003128 A JP 2001003128A JP 17231999 A JP17231999 A JP 17231999A JP 17231999 A JP17231999 A JP 17231999A JP 2001003128 A JP2001003128 A JP 2001003128A
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- Prior art keywords
- thickness
- absorbing member
- recrystallized layer
- strength
- aluminum alloy
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、Ａｌ−Ｍｇ−Ｓｉ
系アルミニウム合金押出材からなり、圧縮の衝撃荷重を
受けたとき、その衝撃荷重を吸収する作用を持つ衝撃吸
収部材に関し、特に自動車のフレーム構造におけるサイ
ドメンバやバンパーステイ及びサイドフレームなどとし
て好適な衝撃吸収部材に関する。TECHNICAL FIELD The present invention relates to an Al-Mg-Si
A shock absorbing member made of extruded aluminum alloy and having a function of absorbing the impact load when subjected to a compression impact load, and particularly suitable as a side member, a bumper stay and a side frame in an automobile frame structure. It relates to an absorbing member.
【０００２】[0002]
【従来の技術】自動車のフレーム構造において、サイド
メンバやバンパーステイなどの衝撃吸収部材として、軽
量化のためアルミニウム合金中空押出材の適用が検討さ
れている。軸方向に圧縮の衝撃荷重を受けるこれらの衝
撃吸収部材には、押出軸方向に荷重を受けたとき形材全
体がオイラー座屈（形材全体がくの字形に曲がる座屈）
を起こさず、かつ圧壊割れを発生することなく蛇腹状に
収縮変形して、安定した高いエネルギー吸収を得るこ
と、及び自動車フレーム構造材として必要な強度（耐
力）を有することが要求される。2. Description of the Related Art In an automobile frame structure, as an impact absorbing member such as a side member or a bumper stay, the use of an aluminum alloy hollow extruded material for weight reduction has been studied. These shock-absorbing members, which receive a compressive impact load in the axial direction, have Euler buckling (buckling in which the entire shape bends in a U-shape) when a load is applied in the extrusion axial direction.
It is required to obtain a stable and high energy absorption by shrinking and deforming in a bellows-like manner without causing cracks and without generating crushing cracks, and to have strength (proof strength) required for a frame material of an automobile.
【０００３】これまで、衝撃吸収部材として利用できる
アルミニウム合金押出材として、高強度アルミニウム合
金の中では比較的耐食性に優れ、リサイクル性の面でも
他の系のアルミニウム合金より優れているＡｌ−Ｍｇ−
Ｓｉ系アルミニウム合金押出材が多く検討されている
（例えば特開平６−２５７８３号公報、特開平７−５４
０９０号公報、特開平７−１１８７８２号公報、特開平
９−２５６０９６号公報等）。Heretofore, as an aluminum alloy extruded material which can be used as a shock absorbing member, Al-Mg- is relatively excellent in corrosion resistance among high-strength aluminum alloys and is also superior in recycling performance to other aluminum alloys.
Many extruded Si-based aluminum alloys have been studied (for example, JP-A-6-25783, JP-A-7-54).
090, JP-A-7-118782, JP-A-9-256096, etc.).
【０００４】上記公報にも記載されているように、Ａｌ
−Ｍｇ−Ｓｉ系アルミニウム合金押出材を衝撃吸収部材
に適用する場合、一般にオンラインによるプレス焼入れ
又はオフラインによる溶体化・焼入れ処理を行った後、
時効処理を施している。ここで時効処理を施すのは、押
出材の強度を向上させ、かつ組織を安定化し使用中に自
然時効が進行して耐圧壊割れ性が劣化するのを防止する
ためである。As described in the above publication, Al
-When applying a Mg-Si based aluminum alloy extruded material to a shock absorbing member, generally after performing online press quenching or offline solution heat treatment,
Aging treatment has been applied. The aging treatment is performed here to improve the strength of the extruded material, stabilize the structure, and prevent the natural aging from progressing during use to prevent the pressure-resistant cracking property from deteriorating.
【０００５】[0005]
【発明が解決しようとする課題】しかし、Ａｌ−Ｍｇ−
Ｓｉ系アルミニウム合金押出材は、サイドメンバー等と
して使用中に高温にさらされ、自然時効が進行し耐圧壊
割れ性が劣化する可能性があり、それを防止するため時
効処理を行うことは熱処理型のＡｌ−Ｍｇ−Ｓｉ系アル
ミニウム合金押出材を衝撃吸収部材として用いる場合の
必須の要件であるが、Ｔ５、Ｔ６処理を行って強度を上
げた場合、軸方向に圧縮変形させたときに圧壊割れが発
生するという問題をはらんでいる。圧壊割れが発生する
と、蛇腹状の収縮変形が妨げられて安定したエネルギー
吸収が得られなくなる。また、最近ではリサイクル性等
の観点から、同じＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金
押出材を、横方向に衝撃荷重を受けるサイドフレームな
ど、その他の自動車フレーム構造材等としても、同時に
利用できるようにすることが求められるようになってき
た。そこで、本発明は、高強度（耐力）を付与したＡｌ
−Ｍｇ−Ｓｉ系アルミニウム合金押出材に、軸方向に優
れた耐圧壊割れ性及び優れたエネルギー吸収性を与え、
同時に横方向にも優れた耐圧壊割れ性を与えることを目
的とする。However, Al-Mg-
Extruded Si-based aluminum alloys are exposed to high temperatures during use as side members, etc., and natural aging may progress and the pressure-resistant cracking and cracking properties may be degraded. This is an essential requirement when the extruded Al-Mg-Si-based aluminum alloy is used as a shock absorbing member. However, when the strength is increased by performing T5 and T6 treatments, when the material is subjected to compressive deformation in the axial direction, it is crushed and cracked. There is a problem that occurs. When the crush crack occurs, the bellows-like contraction deformation is prevented, and stable energy absorption cannot be obtained. Recently, from the viewpoint of recyclability and the like, the same extruded Al-Mg-Si-based aluminum alloy can be used at the same time as other automobile frame structural materials such as side frames that receive a lateral impact load. It has been required to do so. Thus, the present invention provides a method for producing Al with high strength (proof stress).
-To give extruded material of Mg-Si based aluminum alloy with excellent pressure cracking resistance and excellent energy absorption in the axial direction,
At the same time, the object is to provide excellent pressure-resistant cracking resistance in the lateral direction.
【０００６】[0006]
【課題を解決するための手段】Ａｌ−Ｍｇ−Ｓｉ系アル
ミニウム合金押出材において、時効処理後の強度を高く
したいとき、一般にＭｇ、Ｓｉ及び遷移元素（Ｃｕ、Ｍ
ｎ、Ｃｒ、Ｚｒ等）の添加量を多くしているが、その場
合、必然的に粒界の析出物が増して粒界に歪みが集中す
る。また、添加元素量が多いと一般に焼入感受性が鋭く
なり、低い冷却速度（例えば寸法精度やコスト面で有利
な空冷プレス焼入れ）では同じく粒界の析出物の量が増
し、大きい衝撃荷重を受けて圧壊するとき割れが発生し
やすくなる。これに対し、本発明者らは、Ａｌ−Ｍｇ−
Ｓｉ系アルミニウム合金押出材のマクロ組織が再結晶組
織を主体とするものであるとき圧壊割れが発生しやすい
が、繊維状組織（押出による繊維状組織が押出工程以降
の熱処理工程の間においても再結晶することなく、その
まま残った状態の組織）を主体とするとき、高強度でも
圧壊割れの発生が抑えられることを見いだした。一方、
オフラインで溶体化・焼入れを行うと繊維状組織が緩ん
でしまうこと、またオンラインによるプレス焼入れで所
要の特性を得るためには、ある程度の厚さの表面再結晶
層を形成する方が有利であることも分かった。本発明
は、この知見に基づいてなされたものである。When it is desired to increase the strength of an extruded Al-Mg-Si aluminum alloy after aging treatment, it is common to use Mg, Si and transition elements (Cu, M).
(n, Cr, Zr, etc.) is increased, but in that case, precipitates at the grain boundaries inevitably increase and strain concentrates at the grain boundaries. In addition, when the amount of added elements is large, the quenching sensitivity generally becomes sharp. At a low cooling rate (for example, air-cooled press quenching which is advantageous in terms of dimensional accuracy and cost), the amount of precipitates at the grain boundaries increases, and a large impact load is applied. When crushed, cracks are likely to occur. In contrast, the present inventors have proposed Al-Mg-
When the macrostructure of the Si-based aluminum alloy extruded material is mainly composed of a recrystallized structure, crush cracking is likely to occur, but the fibrous structure (the fibrous structure due to extrusion may be regenerated during the heat treatment process after the extrusion process). It has been found that when mainly composed of a structure that remains as it is without crystallization, the occurrence of crush cracking can be suppressed even at high strength. on the other hand,
It is more advantageous to form a surface recrystallized layer of a certain thickness in order to obtain a required property by solution quenching and quenching off-line and to obtain required characteristics by online quenching. I understood that. The present invention has been made based on this finding.
【０００７】本発明に係る耐圧壊性に優れた衝撃吸収部
材は、Ｍｇが０．４０〜０．８０ｗｔ％、Ｓｉ含有量が
０．５０〜１．０ｗｔ％を含み、プレス焼入れ後時効処
理したＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金中空押出材
からなり、耐力２００ＭＰａ以上かつ表面再結晶層厚さ
が肉厚の１〜５０％であり、さらに表面再結晶層の肉厚
方向の結晶粒径は２００μｍ以下であることを特徴とす
る。押出材の表面再結晶層の内側は繊維状組織層であ
る。この衝撃吸収部材は、押出軸方向に圧縮の衝撃荷重
を受けるサイドメンバやバンパーステイに特に好適であ
り、また横方向に圧縮の衝撃荷重を受けるサイドフレー
ムなど、その他の自動車フレーム構造材等としても利用
できる。[0007] The shock absorbing member of the present invention having excellent pressure crush resistance contains 0.40 to 0.80 wt% of Mg and 0.50 to 1.0 wt% of Si, and is subjected to aging treatment after press hardening. It is made of an Al-Mg-Si based aluminum alloy hollow extruded material, has a proof stress of 200 MPa or more, has a surface recrystallized layer thickness of 1 to 50% of the wall thickness, and has a crystal grain size of 200 µm in the thickness direction of the surface recrystallized layer. It is characterized by the following. The inside of the surface recrystallized layer of the extruded material is a fibrous structure layer. This impact absorbing member is particularly suitable for a side member or a bumper stay that receives a compression impact load in the extrusion axial direction, and may also be used as another automobile frame structural material such as a side frame that receives a compression impact load in the lateral direction. Available.
【０００８】[0008]
【発明の実施の形態】上記Ａｌ−Ｍｇ−Ｓｉ系アルミニ
ウム合金は、上記以外の添加元素として必要に応じてＣ
ｕ、Ｍｎ、Ｃｒ、Ｚｒ、Ｔｉ、不可避不純物としてＦ
ｅ、その他の元素を含むことができる。以下、本発明の
衝撃吸収部材を構成する押出材の組成等について説明す
る。BEST MODE FOR CARRYING OUT THE INVENTION The above Al-Mg-Si based aluminum alloy may be used as an additional
u, Mn, Cr, Zr, Ti, F as inevitable impurities
e, may contain other elements. Hereinafter, the composition and the like of the extruded material constituting the shock absorbing member of the present invention will be described.
【０００９】Ｍｇ、Ｓｉ ＭｇとＳｉは結合してＭｇ２Ｓｉを形成し、合金強度を
向上させる。自動車フレーム構造材として必要な強度を
得るためには、Ｍｇは０．４０％以上の添加が必要であ
る。しかし、０．８０％を越えて添加されると焼入れ感
受性が鋭くなり、焼入れ速度が低くなると焼きが入らず
必要な強度が出なくなる。従って、Ｍｇ含有量は０．４
０〜０．８０％とする。より望ましい範囲は０．４０〜
０．６０％である。一方、Ｓｉ量が０．５０％より少な
いと必要な強度が得られず、１．０％を越えると焼入れ
感受性が鋭くなり、同じく焼入れ速度が低くなると焼き
が入らず必要な強度が出なくなる。従って、Ｓｉ含有量
は０．５０〜１．０％とする。このＭｇ及びＳｉ量の範
囲内で、高い強度が得られ焼入れ感受性が余り鋭くなら
ない範囲として、Ｓｉ量は０．５０〜０．７０％が特に
望ましい。Mg, Si Mg and Si combine to form Mg 2 Si and improve the alloy strength. In order to obtain the strength required for an automobile frame structural material, Mg must be added in an amount of 0.40% or more. However, if added in excess of 0.80%, the quenching sensitivity becomes sharp, and if the quenching speed is reduced, quenching does not occur and the required strength cannot be obtained. Therefore, the Mg content is 0.4
0 to 0.80%. A more desirable range is 0.40
0.60%. On the other hand, if the Si content is less than 0.50%, the required strength cannot be obtained, and if it exceeds 1.0%, the quenching sensitivity becomes sharp, and if the quenching speed is low, the quenching does not occur and the required strength cannot be obtained. Therefore, the Si content is set to 0.50 to 1.0%. Within the range of the amounts of Mg and Si, the amount of Si is particularly preferably 0.50 to 0.70% as a range in which high strength is obtained and quenching sensitivity is not so sharp.
【００１０】Ｍｎ、Ｃｒ、Ｚｒ Ｍｎ、Ｃｒ、Ｚｒは押出材に繊維状組織を形成して耐圧
壊割れ性を向上させる作用があり、これらの中から１種
又は２種以上が、Ｍｎ：０．０５〜０．４０％、Ｃｒ：
０．０５〜０．２０％、Ｚｒ：０．０５〜０．２０％の
範囲で添加される。これらの遷移元素の添加量が下限未
満では繊維状組織とならないか、表面再結晶層が厚く出
て圧壊割れが発生し、上限を越えると焼入れ感受性が鋭
くなり、焼入れ速度が低いとき焼きが入らず、自動車フ
レーム構造材として必要な強度が出なくなる。このとき
各元素の望ましい範囲は、Ｍｎ：０．０５〜０．２５
％、Ｃｒ：０．０５〜０．１５％、Ｚｒ：０．０５〜
０．１５％である。また、これらの遷移元素の合計添加
量は０．０５〜０．６０％とし、０．１０〜０．４０％
がより望ましく、さらに０．２〜０．３％が望ましい。Mn, Cr, Zr Mn, Cr, Zr have the effect of forming a fibrous structure in the extruded material to improve the pressure-resistant cracking resistance. 0.05 to 0.40%, Cr:
It is added in the range of 0.05 to 0.20% and Zr: 0.05 to 0.20%. If the added amount of these transition elements is less than the lower limit, a fibrous structure will not be formed, or the surface recrystallized layer will be thick and crush cracking will occur. As a result, the strength required for an automobile frame structural material cannot be obtained. At this time, a desirable range of each element is Mn: 0.05 to 0.25.
%, Cr: 0.05-0.15%, Zr: 0.05-
0.15%. The total amount of these transition elements is 0.05 to 0.60%, and 0.10 to 0.40%
Is more desirable, and more preferably 0.2 to 0.3%.
【００１１】Ｃｕ ＣｕはＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金の強度を高
め、耐応力腐食割れ性を改善する作用があり、必要に応
じて添加される。しかし、０．０５％未満では作用が不
十分であり、０．７％を越えると押出性及び一般耐食性
が低下するので、含有量は０．０５〜０．７％が望まし
い。より望ましい範囲は０．１０〜０．３５％である。 Ｔｉ Ｔｉは、鋳塊組織を微細化する作用があり、適宜添加さ
れる。しかし、０．００５％より少ないと微細化の効果
が十分でなく、０．２％より多いと飽和して巨大化合物
が発生してしまう。従って、Ｔｉの含有量は０．００５
〜０．２％とする。より望ましい範囲は０．０１〜０．
１０％、さらに望ましい範囲は０．０１５〜０．０５％
である。Cu Cu has the effect of increasing the strength of an Al-Mg-Si-based aluminum alloy and improving stress corrosion cracking resistance, and is added as necessary. However, if the content is less than 0.05%, the effect is insufficient, and if it exceeds 0.7%, the extrudability and the general corrosion resistance decrease, so that the content is desirably 0.05 to 0.7%. A more desirable range is 0.10 to 0.35%. Ti Ti has an effect of refining the ingot structure, and is appropriately added. However, if it is less than 0.005%, the effect of miniaturization is not sufficient, and if it is more than 0.2%, it is saturated and a giant compound is generated. Therefore, the content of Ti is 0.005.
To 0.2%. A more desirable range is from 0.01 to 0.1.
10%, more preferably 0.015 to 0.05%
It is.
【００１２】不可避不純物 不可避不純物のうちＦｅはアルミニウム地金に最も多く
含まれる不純物であり、０．３５％を超えて合金中に存
在すると鋳造時に粗大な金属間化合物を晶出し、合金の
機械的性質を損なう。従って、Ｆｅの含有量は０．３５
％以下に規制する。望ましくは０．３０％以下であり、
さらに０．２５％以下が望ましい。また、アルミニウム
合金を鋳造する際には地金、添加元素の中間合金等様々
な経路より不純物が混入する。混入する元素は様々であ
るが、Ｆｅ以外の不純物は単体で０．０５％以下、総量
で０．１５％以下であれば合金の特性にほとんど影響を
及ぼさない。従って、これらの不純物は単体で０．０５
％以下、総量で０．１５％以下とする。なお、不純物の
うちＢについてはＴｉの添加に伴い合金中にＴｉ含有量
の１／５程度の量で混入するが、より望ましい範囲は
０．０２％以下、さらに０．０１％以下が望ましい。Inevitable impurities Fe is the most inevitable impurity contained in aluminum ingots. If it exceeds 0.35% in the alloy, coarse intermetallic compounds are crystallized during casting, and the mechanical properties of the alloy are reduced. Impair the nature. Therefore, the content of Fe is 0.35
% Or less. Desirably 0.30% or less,
Further, it is desirably 0.25% or less. Further, when casting an aluminum alloy, impurities are mixed from various routes such as a base metal and an intermediate alloy of an additive element. There are various elements to be mixed, but impurities other than Fe alone have 0.05% or less, and if the total amount is 0.15% or less, it hardly affects the properties of the alloy. Therefore, these impurities alone are 0.05%
% Or less, and a total amount of 0.15% or less. In addition, B among impurities is mixed into the alloy in an amount of about 1/5 of the Ti content with the addition of Ti, but a more desirable range is 0.02% or less, and further preferably 0.01% or less.
【００１３】強度（耐力） 自動車フレーム構造材（衝撃吸収部材）としての適用を
考えた場合、強度が２００ＭＰａに満たないとエネルギ
ー吸収量が低下するため、強度は２００ＭＰａ以上が必
要である。しかし、上記組成を外れるとその強度が出な
くなるか（エネルギー吸収量も大きく低下する）、繊維
状組織が形成されず耐圧壊割れ特性に劣るようになる。
耐力の望ましい範囲は２２０ＭＰａ以上である。Strength (Strength) In consideration of application as a structural material (impact absorbing member) for an automobile frame, if the strength is less than 200 MPa, the amount of energy absorption is reduced, so the strength needs to be 200 MPa or more. However, if the composition is out of the above range, the strength will not be obtained (the amount of energy absorption will be greatly reduced), or a fibrous structure will not be formed and the pressure cracking characteristics will be inferior.
A desirable range of the proof stress is 220 MPa or more.
【００１４】表面再結晶層 上記Ａｌ−Ｍｇ−Ｓｉ系アルミニウム合金押出材におい
て、押出材の繊維状組織は押出材の断面のほぼ全体に形
成されているのが望ましく、自動車フレーム構造材のよ
うに厚さ１〜５ｍｍの押出材であれば、表面再結晶層は
全体の肉厚の５０％以下とする必要がある。望ましくは
３０％以下である。これは、再結晶粒は繊維状組織に比
べて結晶粒径が大きいことと、冷却速度が低い場合は冷
却過程で結晶粒界に析出する析出物が多くなり、表面再
結晶粒の粒界に歪みが集中して割れが発生しやすくなる
ためである。一方、上記組成及び厚さのＡｌ−Ｍｇ−Ｓ
ｉ系アルミニウム合金押出材であれば、５ｍ／分以下の
押出速度で押出材の断面のほぼ全て（表面再結晶層厚さ
が肉厚の１％未満）繊維状組織とすることができるが、
このような低い押出速度ではプレス焼入れ（オンライ
ン）において焼入れゾーンに入るまでに時間がかかるた
め、焼きが入りにくく必要な強度、エネルギー吸収量及
び最大荷重が得にくくなる。従って、表面再結晶層厚さ
は肉厚の１％以上とする必要がある。望ましくは５％以
上である。また、表面再結晶粒の結晶粒径は２００μｍ
以下、さらに１００μｍ以下とするのが望ましい。これ
は、表面再結晶粒の粒径が大きいほど歪みが集して割れ
が発生しやすくなるためである。Surface Recrystallized Layer In the Al-Mg-Si aluminum alloy extruded material, it is desirable that the fibrous structure of the extruded material is formed on almost the entire cross section of the extruded material. In the case of an extruded material having a thickness of 1 to 5 mm, the surface recrystallized layer needs to be 50% or less of the entire thickness. Desirably, it is 30% or less. This is because the recrystallized grains have a larger crystal grain size than the fibrous structure, and when the cooling rate is low, the precipitates that precipitate at the crystal grain boundaries during the cooling process increase, and This is because strain is concentrated and cracks are likely to occur. On the other hand, the above composition and thickness of Al-Mg-S
If it is an i-type aluminum alloy extruded material, almost all of the cross section of the extruded material (the thickness of the surface recrystallized layer is less than 1% of the wall thickness) can be formed into a fibrous structure at an extrusion speed of 5 m / min or less.
At such a low extrusion speed, it takes time to enter the quenching zone in press quenching (on-line), so that quenching is difficult and the necessary strength, energy absorption, and maximum load are difficult to obtain. Therefore, the thickness of the surface recrystallized layer needs to be 1% or more of the wall thickness. Desirably, it is 5% or more. The crystal grain size of the surface recrystallized grains is 200 μm.
Hereinafter, it is more preferable that the thickness be 100 μm or less. This is because the larger the grain size of the surface recrystallized grains, the more the strain is gathered and the more easily the cracks are generated.
【００１５】[0015]
【実施例】以下、本発明の実施例について説明する。Ｄ
Ｃ鋳造により、表１に示す成分組成のＡｌ−Ｍｇ−Ｓｉ
系アルミニウム合金ビレットを溶製し、５５０℃×４ｈ
ｒの均熱処理を行った。続いて、押出温度５００℃及び
表１に示す押出速度で押出加工を行い、押出直後にオン
ラインで空冷又は水冷によるプレス焼入れを行い、図１
に示すような中空矩形断面の押出材（長辺が７０〜８０
ｍｍ、短辺が５４〜６０ｍｍ、肉厚が２〜５ｍｍ）を得
た。なお、空冷はファン空冷で冷却速度：約１９０℃／
ｍｉｎ、水冷は冷却速度：約１００００℃／ｍｉｎであ
った。ついで、この押出材に対し１９０℃×３時間の時
効処理を施し、供試材とした。Embodiments of the present invention will be described below. D
Al-Mg-Si having the composition shown in Table 1 by C casting
550 ° C × 4h
r was soaked. Subsequently, extrusion was performed at an extrusion temperature of 500 ° C. and an extrusion speed shown in Table 1. Immediately after the extrusion, online press quenching by air cooling or water cooling was performed.
Extruded material having a hollow rectangular cross section as shown in FIG.
mm, the short side is 54 to 60 mm, and the wall thickness is 2 to 5 mm). In addition, the air cooling is a fan air cooling and the cooling rate is about 190 ° C. /
min, water cooling was a cooling rate of about 10,000 ° C./min. Next, this extruded material was subjected to aging treatment at 190 ° C. for 3 hours to obtain a test material.
【００１６】この供試材について、表面再結晶層（ＧＧ
層）厚さ、表面再結晶層の結晶粒径、機械的特性、縦及
び横方向圧壊特性を下記要領で調べた。その結果を表１
及び表２に示す。 表面再結晶層厚さ：押出方向に平行方向の断面におい
て、表面４箇所及び裏面４箇所をとり、それぞれの再結
晶層厚を測定し、表裏各々平均をとり、表の平均値と裏
の平均値の合計をＧＧ層厚さとした。 表面再結晶層粒径：押出方向に平行方向の断面におい
て、表面から肉厚中心部へ向かって切断法にて、表側４
箇所、裏側４箇所測定し、その平均をとってＧＧ層粒径
とした。ここで、粒径を表面から肉厚中心部へ向かって
測定するのは、この方向に測定した粒径が割れの発生に
特に関係するためである。（なお、本発明では、表面再
結晶層厚さが表面再結晶層粒径より十分大きくなく粒径
の測定が難しい場合は、表面再結晶層粒径＝表面再結晶
層厚さと定義する。） 機械的特性：供試材よりＪＩＳ５号試験片を採取し、Ｊ
ＩＳ Ｚ ２２４１に準拠して引張試験を行った。For this test material, a surface recrystallized layer (GG
Layer) The thickness, the crystal grain size of the surface recrystallized layer, the mechanical properties, and the longitudinal and lateral crushing properties were examined in the following manner. Table 1 shows the results.
And Table 2. Surface recrystallized layer thickness: In a cross section parallel to the extrusion direction, four front surfaces and four back surfaces are measured, the recrystallized layer thicknesses are measured, the average of each of the front and back sides is taken, and the average value of the front and back sides is averaged. The sum of the values was defined as the GG layer thickness. Surface recrystallized layer particle size: In the cross section parallel to the extrusion direction, the front side 4
And the back side were measured at four points, and the average was taken as the GG layer particle size. Here, the reason why the particle size is measured from the surface toward the center of the thickness is that the particle size measured in this direction is particularly related to the occurrence of cracks. (In the present invention, when the thickness of the surface recrystallized layer is not sufficiently larger than the particle size of the surface recrystallized layer and it is difficult to measure the particle size, the particle size of the surface recrystallized layer is defined as the surface recrystallized layer thickness.) Mechanical properties: A JIS No. 5 test piece was collected from the test material,
A tensile test was performed according to IS Z 2241.
【００１７】縦圧縮特性：長さ２００ｍｍの供試材を用
い、アムスラー試験機にて図２に示すように軸方向に静
的圧縮荷重を加え、これを１００ｍｍまで圧縮して荷重
−変位曲線を得、最大荷重と１００ｍｍまでの吸収エネ
ルギーを求めた。割れ性の評価は目視にて行い、割れの
発生していないものを◎、微小な割れの発生したものを
○、開口割れの発生したものを×と評価した。 横圧縮特性：長さ２００ｍｍの供試材を用い、図３に示
すように長辺側が上下になるように横向きに置いて静的
圧縮荷重を加え、これを２０ｍｍまで圧縮し、割れ性の
評価を目視にて行った。割れの発生していないものを
◎、微小な割れの発生したものを○、開口割れの発生し
たものを×と評価した。Longitudinal compression characteristics: Using a test material having a length of 200 mm, a static compressive load was applied in the axial direction by an Amsler tester as shown in FIG. 2, and this was compressed to 100 mm to obtain a load-displacement curve. Then, the maximum load and the absorbed energy up to 100 mm were determined. The evaluation of the cracking property was carried out by visual observation, and those without cracks were evaluated as ◎, those with minute cracks as ○, and those with opening cracks as x. Lateral compression characteristics: Using a test material having a length of 200 mm, a static compressive load was applied by placing the sample sideways so that the long side was up and down as shown in FIG. Was performed visually. The case where no cracks occurred was evaluated as ◎, the case where minute cracks occurred was evaluated as ○, and the case where opening cracks occurred was evaluated as x.
【００１８】[0018]
【表１】 [Table 1]
【００１９】[0019]
【表２】 [Table 2]
【００２０】表２に示すように、ＧＧ層厚さが本発明の
規定範囲内のもの（Ｎｏ．１〜８）は圧壊割れを起こさ
ず、高い耐力及び優れたエネルギー吸収特性（縦横とも
に圧壊割れなし、高い吸収エネルギー及び最大荷重）を
示す。一方、表面ＧＧ層が形成されていないＮｏ．９は
耐力が２００ＭＰａに満たず、吸収エネルギー及び最大
荷重が低く、ＧＧ層厚さが本発明の規定範囲を超えるも
の（Ｎｏ．１０〜１５）は圧壊割れ性が劣り、ＧＧ層厚
さが本発明の規定範囲内でも、耐力が２００ＭＰａに達
しないＮｏ．１６は吸収エネルギー及び最大荷重が低
く、ＧＧ層粒径が２００μｍを超えるＮｏ．１７は圧壊
割れ性が劣る。As shown in Table 2, those having a GG layer thickness within the specified range of the present invention (Nos. 1 to 8) did not cause crushing cracks, had high proof stress and excellent energy absorption characteristics (crushing cracks in both longitudinal and transverse directions). None, high absorbed energy and maximum load). On the other hand, No. 1 having no surface GG layer was formed. No. 9 has a yield strength of less than 200 MPa, a low absorbed energy and a maximum load, and a GG layer thickness exceeding the specified range of the present invention (Nos. 10 to 15) has inferior crush cracking properties and a GG layer thickness of No. 2 whose proof stress does not reach 200 MPa even within the specified range of the invention. No. 16 has a low absorption energy and a maximum load and has a GG layer particle size exceeding 200 μm. No. 17 is inferior in crush cracking property.
【００２１】[0021]
【発明の効果】本発明によれば、Ａｌ−Ｍｇ−Ｓｉ系ア
ルミニウム合金押出材について、耐力と表面再結晶層の
割合、及び粒径を規定することにより、高強度で優れた
エネルギー吸収特性を示す衝撃吸収部材を得ることがで
きる。According to the present invention, high strength and excellent energy absorption characteristics can be obtained by specifying the proof stress, the ratio of the surface recrystallized layer, and the particle size of the extruded Al-Mg-Si aluminum alloy. The shock absorbing member shown can be obtained.
【図１】 実施例に用いた押出材の断面形状を示す図で
ある。FIG. 1 is a diagram showing a cross-sectional shape of an extruded material used in an example.
【図２】 実施例の縦圧壊試験を説明する図（圧壊前、
圧壊後）である。FIG. 2 is a view for explaining a longitudinal crush test of an embodiment (before crush,
After crushing).
【図３】 実施例の横圧壊試験を説明する図（圧壊前、
圧壊後）である。FIG. 3 is a view for explaining a lateral crush test of an example (before crush,
After crushing).
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ テーマコート゛(参考） Ｃ２２Ｆ 1/00 ６０４ Ｃ２２Ｆ 1/00 ６０４ ６１２ ６１２ ６２６ ６２６ ６３０ ６３０Ｂ ６８３ ６８３ ６８４ ６８４Ｚ ──────────────────────────────────────────────────続 き Continued on the front page (51) Int.Cl. 7 Identification symbol FI Theme coat ゛ (Reference) C22F 1/00 604 C22F 1/00 604 612 612 626 626 626 630 630B 683 683 684 684Z
Claims (1)
含有量が０．５０〜１．０ｗｔ％を含み、プレス焼入れ
後時効処理したＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金中
空押出材からなり、耐力２００ＭＰａ以上かつ表面再結
晶層厚さが肉厚の１〜５０％であり、さらに表面再結晶
層の肉厚方向の結晶粒径が２００μｍ以下であることを
特徴とする耐圧壊割れ性に優れた衝撃吸収部材。1. An alloy containing 0.40 to 0.80 wt% of Mg,
It is composed of an Al-Mg-Si-based aluminum alloy hollow extruded material containing 0.50 to 1.0 wt% and aging treatment after press quenching, with a proof stress of 200 MPa or more and a surface recrystallized layer thickness of 1 to 1 An impact-absorbing member excellent in pressure-resistant cracking resistance, characterized in that the thickness is 50% and the crystal grain size in the thickness direction of the surface recrystallized layer is 200 μm or less.
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17231999A JP3454755B2 (en) | 1999-06-18 | 1999-06-18 | Shock absorbing member with excellent pressure-resistant cracking resistance |
| EP00107024A EP1041165A1 (en) | 1999-04-02 | 2000-03-31 | Shock absorbing material |
| US10/190,483 US20030008165A1 (en) | 1999-04-02 | 2002-07-09 | Shock absorbing material |
| US10/420,756 US20030207143A1 (en) | 1999-04-02 | 2003-04-23 | Shock absorbing material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17231999A JP3454755B2 (en) | 1999-06-18 | 1999-06-18 | Shock absorbing member with excellent pressure-resistant cracking resistance |
Related Child Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2002272315A Division JP2003183757A (en) | 2002-09-18 | 2002-09-18 | Shock-absorbing member showing excellent crush resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2001003128A true JP2001003128A (en) | 2001-01-09 |
| JP3454755B2 JP3454755B2 (en) | 2003-10-06 |
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ID=15939719
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP17231999A Expired - Lifetime JP3454755B2 (en) | 1999-04-02 | 1999-06-18 | Shock absorbing member with excellent pressure-resistant cracking resistance |
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| Country | Link |
|---|---|
| JP (1) | JP3454755B2 (en) |
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| FR2917428A1 (en) * | 2007-06-18 | 2008-12-19 | Alcan Int Ltd | PROCESS FOR PRODUCING AN ALUMINUM ALLOY SEMI-PRODUCT, IN PARTICULAR FOR A MOTOR VEHICLE STRUCTURE |
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| US7444062B2 (en) | 2004-01-09 | 2008-10-28 | Canon Kabushiki Kaisha | Playback system |
| FR2917428A1 (en) * | 2007-06-18 | 2008-12-19 | Alcan Int Ltd | PROCESS FOR PRODUCING AN ALUMINUM ALLOY SEMI-PRODUCT, IN PARTICULAR FOR A MOTOR VEHICLE STRUCTURE |
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