JP3834957B2 - Manufacturing method of light metal alloy forged products - Google Patents
Manufacturing method of light metal alloy forged products Download PDFInfo
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- JP3834957B2 JP3834957B2 JP26388897A JP26388897A JP3834957B2 JP 3834957 B2 JP3834957 B2 JP 3834957B2 JP 26388897 A JP26388897 A JP 26388897A JP 26388897 A JP26388897 A JP 26388897A JP 3834957 B2 JP3834957 B2 JP 3834957B2
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- 229910001092 metal group alloy Inorganic materials 0.000 title claims description 15
- 238000004519 manufacturing process Methods 0.000 title claims description 6
- 238000010438 heat treatment Methods 0.000 claims description 25
- 239000011777 magnesium Substances 0.000 claims description 25
- 238000000265 homogenisation Methods 0.000 claims description 24
- 239000012071 phase Substances 0.000 claims description 23
- 239000000463 material Substances 0.000 claims description 22
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 21
- 229910052749 magnesium Inorganic materials 0.000 claims description 21
- 239000007790 solid phase Substances 0.000 claims description 18
- 238000002347 injection Methods 0.000 claims description 17
- 239000007924 injection Substances 0.000 claims description 17
- 239000013078 crystal Substances 0.000 claims description 16
- 229910052782 aluminium Inorganic materials 0.000 claims description 14
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 14
- 238000000034 method Methods 0.000 claims description 11
- 150000001875 compounds Chemical class 0.000 claims description 10
- 238000005242 forging Methods 0.000 claims description 10
- 229910045601 alloy Inorganic materials 0.000 claims description 9
- 239000000956 alloy Substances 0.000 claims description 9
- 239000007791 liquid phase Substances 0.000 claims description 6
- 229910020068 MgAl Inorganic materials 0.000 claims description 5
- 239000010953 base metal Substances 0.000 claims 1
- 238000001746 injection moulding Methods 0.000 description 15
- 229910000861 Mg alloy Inorganic materials 0.000 description 13
- 230000000694 effects Effects 0.000 description 9
- 239000002245 particle Substances 0.000 description 8
- 238000005266 casting Methods 0.000 description 6
- 229910001234 light alloy Inorganic materials 0.000 description 5
- 239000012778 molding material Substances 0.000 description 5
- 238000009749 continuous casting Methods 0.000 description 3
- 238000011156 evaluation Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 239000007787 solid Substances 0.000 description 3
- 230000007423 decrease Effects 0.000 description 2
- 238000004512 die casting Methods 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 229910018137 Al-Zn Inorganic materials 0.000 description 1
- 229910018573 Al—Zn Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
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Description
【０００１】
【発明の属する技術分野】
本発明は、軽金属合金、特に合金成分としてアルミニウムを含有するマグネシウム合金の成形性に優れた軽金属合金鍛造製品の製造方法に関する。
【０００２】
【従来の技術】
アルミニウムまたはマグネシウムを母材とする軽金属合金、特にアルミニウムを合金成分とするマグネシウム合金は軽量でかつ鍛造等の塑性加工を施すことにより所定の機械的強度を確保できる素材として注目されている。しかしながら、通常の溶解鋳造法で型内に鋳込んだ鋳造品は鍛造等の塑性加工性に欠け、所定の機械的強度を確保するのが難しい。
【０００３】
【発明が解決しようとする課題】
そこで、アルミニウムおよびマグネシムを含有する軽金属合金においてかかる塑性加工性に欠ける原因を探求すると、第１に、アルミニウムおよびマグネシムが併存する場合は粒界にＡｌ12Ｍｇ17で示される化合物が生成し、これが塑性加工性に影響を与える。他方、溶解鋳造法で鋳込んだ鋳造品にはマグネシム初晶α相がないが、固相／液相が共存する半溶融状態で射出成形した成形品にはマグネシム初晶α相が存在する。したがって、この初晶α相の存否が上記ＡｌＭｇ化合物の影響を緩和し、塑性加工性の向上に影響を与えるものと思われる。
第２に、上記マグネシウムの初晶α相の粒径は固相／液相比率である固相率が小さくなるに伴い小さくなるが、それだけでは塑性加工性の向上はそれほど認められない。しかしながら、均質化熱処理に付する場合、短時間処理で塑性加工性が著しく向上することが見出された。これは溶解鋳造法では認められなかった効果である。
【０００４】
そこで、本発明の第１の目的は、塑性加工性を向上させるマグネシウムの初晶α相を有する軽金属合金射出成形材およびその製造方法並びに軽合金鍛造製品を提供することにある。
本発明の第２の目的は均質化熱処理により塑性加工性を向上させることができる軽金属合金射出成形材およびその製造方法並びに軽合金鍛造製品を提供することにある。
【０００５】
【問題を解決するための手段】
上記目的を達成するため、本発明は母材がマグネシウムであって、合金成分として少なくともアルミニウム５質量％以上を含有する軽金属合金を固相／液相が共存する半溶融状態であって固相率７０％以下の半溶融状態とした後、射出成形して平均結晶粒径２００μｍ以下並びにマグネシウム初晶α相が粒径１２０μｍ以下の成形物となし、その成形物を３００〜５００℃×３０分〜１０時間の範囲内で均質化熱処理して、射出成形品の粒界に存在するＭｇＡｌ化合物を母材に固溶させ、該射出成形品を鍛造工程に付することを特徴とする軽金属合金鍛造製品の製造方法を提供するものである。
マグネシウムの初晶α相を生成させるためには射出成形を半溶融射出成形法に基づいて行う必要がある。ここで、半溶融射出成形法による射出成形とは、固相／液相が共存する半溶融状態とした後、射出成形することをいう。
【０００６】
母材がマグネシウムである場合は、合金成分として少なくともアルミニウム５質量％以上を含有し、平均結晶粒径２００μｍ以下であるのが好ましい。
アルミニウムが５質量％未満では、所定の機械強度が得られないからである。したがって、本発明において好ましいマグネシウム合金としては、ＡＳＴＭ規格のＡＺ６１，ＡＺ８０，ＡＺ９１等、Ｍｇ−Ａｌ−Ｚｎ系合金が挙げられる。また、平均結晶粒径が２００μｍ以上では塑性加工性の一つである鍛造時の限界据え込み率５０％以下となるためである。
【０００７】
特に、マグネシウム初晶α相が粒径１２０μｍ以下であって、均質化熱処理にて実質的にＭｇＡｌ化合物を母材に固溶してなる射出成形材は従来の溶解鋳造法では得られなかった成形性の向上が認められ（図１参照）、射出成形材を直接鍛造成形に付すことが可能で、鍛造に至るプロセスを簡略化することができる。
【０００９】
本発明方法は、特に軽金属合金が母材がマグネシウムであって、合金成分として少なくともアルミニウム５質量％以上を含有する場合に有効であり、固相率７０％以下の半溶融状態で射出成形されると、マグネシウム初晶α相が粒径１２０μｍ以下となり、均質化熱処理効果が発揮されるようになる（図１参照）。
【００１０】
均質化熱処理の条件は射出成形品の粒界に存在するＭｇＡｌ化合物を母材に固溶させるに十分な３００〜５００℃×３０分〜１０時間の範囲内で選ばれる。すなわち、ＭｇＡｌ化合物の粒径及び（合金成分に関係する）量、成形品の質量などを考慮すべきである。
【００１１】
本発明によって得られる軽金属合金射出成形材は限界据込み率６０％以上の成形性を有するので、直接鍛造工程に付し軽合金鍛造製品を製造することができる。
【００１２】
【発明の実施の形態】
以下、本発明の実施の形態について、図面を参照しながら説明する。
以下の組成を有するＡＺ８０のマグネシウム合金を用意し、図３に示す半溶融射出成形機（型式：ＪＬＭ−４５０Ｅ，株式会社日本製鋼所製）を用いて次の条件下に射出成形を行った。この射出成形機は成形材料の固相線温度より上であって液相線温度より下の温度にスクリュー押出機中で合金を加熱して半溶融状態とし、高速射出機構により金型キャビティ内にショットするものである。
【００１３】
【表１】
マグネシウム合金組成
（単位：質量％）
Ａｌ Ｚｎ Ｍｎ Ｆｅ Ｓｉ Ｃｕ Ｎｉ Ｍｇ
合金Ａ 8.1 0.45 0.27 0.0018 0.03 0.0025 0.0009 Bal.
【００１４】
【表２】
マグネシウム合金は切削して切粉状となし、ホッパーに投入されるが、固相率（固相／液相）はシリンダー内の加熱温度で調整した。
種々の固相率における射出成形品の初晶α相の成否を顕微鏡写真で確認するとともにその平均粒径を測定した。結果は以下の表３の通りである。
【００１６】
また、上記射出成形したままの材料と均質化熱処理（４００℃×１８０分間）後空冷した材料とを以下の鍛造成形性評価方法により試験した。その結果、固相率７０％以下で初晶α相１２０μｍ以下となり、固相率の低下とともに初晶α相の粒径は小さくなるが、成形性の向上はほとんど見られない。しかしながら、初晶α相が１２０μｍ以下から均質化熱処理効果が発揮され、初晶α相の粒径が小さくなる程その向上は著しいことが分かった。
上記鍛造成形性評価方法としては、円柱状テストピースを用いた据え込み試験により求めた限界据え込み率により評価する方法を用いた。即ち、直径１６ｍｍ、高さ２４ｍｍの円柱状テストピースを、高さ方向に据え込み鍛造し、テストピースの割れが生じる時の高さＨを測定し、以下の式（I）
【数１】
限界据え込み率（％）＝（（２４−Ｈ）／２４）×１００ （I）
より限界据え込み率を求めて評価した。
【００１７】
【表３】
【００１８】
以上の結果をグラフにすると図１に示す通りである。また、均質化熱処理前後の成形性の変化を固相率１０％と７０％の場合と同一組成のマグネシウム合金を連続鋳造した場合とを比較すると図２に示す通りである。すなわち、本発明以外では初晶α相の存在が認められないので、均質化熱処理の効果は認められず、本発明の場合でも固相率７０％以下で均質化熱処理効果が発揮され始め、固相率が低下するぼど初晶α相の粒径が小さくなり、次第に成形性が向上することが認められる。
【００１９】
上記マグネシウム合金を用い、固相率１０％で射出成形した半溶融射出成形材Ａ（図４）、固相率７０％で射出成形した半溶融射出成形材Ｂ（図５）、ダイカストした場合Ｃ（図６）および金型鋳造（連続鋳造）した場合Ｄ（図７）を比較すると、前二者では初晶α相が認められるのに、後二者の場合は初晶α相が認められない。
【００２０】
また、上記半溶融射出成形材ＡおよびＢでは４００℃で３時間という比較的短い均質化熱処理で粒界に存在するＭｇ17Ａｌ12化合物がほとんど固溶して消失する（図８および図９参照）のに対し、金型鋳造材Ｄの場合は４００℃で６時間均質化熱処理を施してもほとんど固溶しない（図１０参照）。この結果は均質化熱処理の成形性の向上の存否に現れている。
【００２１】
以上ＡＺ８０マグネシウム合金について種々の効果を確認したが、このマグネシウムの初晶α相はマグネシウムとアルミニウムを含有する軽合金を半溶融射出成形法で射出成形する限り晶出するものである。また、マグネシウムとアルミニウムを含有する軽金属合金を溶解鋳造する限り粒界に存在するＭｇ17Ａｌ12化合物が析出する。したがって、本発明方法は広くマグネシウムとアルミニウムを含有する軽金属合金に適用可能である。
【００２２】
【発明の効果】
以上説明したように本発明によれば、少なくともマグネシウムとアルミニウムとを含む軽合金において、射出成形によりマグネシウムの初晶α相が存在し、連続鋳造に比して優れた成形性を示す。特に上記初晶α相が１２０μｍ以下の場合は、粒界に析出するＭｇ17Ａｌ12化合物が均質化熱処理により母材に固溶して消失するので、より優れた成形性を示すことになる。
このような本発明射出成形材を用いることにより鍛造成形が容易になり、マグネシウム合金の鍛造品を提供することができる。
【図面の簡単な説明】
【図１】 ＡＺ８０マグネシウム合金の半溶融射出成形における固相率と初晶α相の平均粒径、均質化熱処理前後の成形性の関係を示すグラフ。
【図２】 本発明による均質化熱処理前後の成形性に及ぼす効果と連続鋳造における均質化熱処理前後の成形性に及ぼす効果とを対比したグラフ。
【図３】 本発明で用いる半溶融成形機の概略図である。
【図４】 固相率１０％で射出成形した半溶融射出成形材Ａの組織を示す顕微鏡写真である。
【図５】 固相率７０％で射出成形した半溶融射出成形材Ｂの組織を示す顕微鏡写真である。
【図６】 ＡＺ８０マグネシウム合金のダイカスト材の組織を示す顕微鏡写真である。
【図７】 ＡＺ８０マグネシウム合金の金型鋳造材の組織を示す顕微鏡写真である。
【図８】 図４で示す半溶融射出成形材を均質化熱処理した後の組織を示す顕微鏡写真である。
【図９】 図５で示す半溶融射出成形材を均質化熱処理した後の組織を示す顕微鏡写真である。
【図１０】 図７で示す半溶融射出成形材を均質化熱処理した後の組織を示す顕微鏡写真である。[0001]
BACKGROUND OF THE INVENTION
The present invention relates to a method for producing a light metal alloy forged product excellent in formability of a light metal alloy, particularly a magnesium alloy containing aluminum as an alloy component.
[0002]
[Prior art]
A light metal alloy containing aluminum or magnesium as a base material, particularly a magnesium alloy containing aluminum as an alloy component, is attracting attention as a material that is lightweight and can secure a predetermined mechanical strength by performing plastic working such as forging. However, a cast product cast in a mold by a normal melt casting method lacks plastic workability such as forging, and it is difficult to ensure a predetermined mechanical strength.
[0003]
[Problems to be solved by the invention]
Therefore, when searching for the cause of lack of plastic workability in light metal alloys containing aluminum and magnesium, first, when aluminum and magnesium coexist, a compound represented by Al 12 Mg 17 is formed at the grain boundary. Affects plastic workability. On the other hand, a cast product cast by the melt casting method does not have a magnesium primary crystal α phase, but a molded product injection-molded in a semi-molten state in which a solid phase / liquid phase coexist has a magnesium primary crystal α phase. Therefore, it is considered that the presence or absence of the primary α phase relaxes the influence of the AlMg compound and affects the improvement of plastic workability.
Secondly, the particle size of the primary α phase of magnesium becomes smaller as the solid phase ratio, which is the solid phase / liquid phase ratio, becomes smaller. However, it has been found that when subjected to a homogenization heat treatment, the plastic workability is significantly improved in a short time treatment. This is an effect that was not recognized by the melt casting method.
[0004]
Accordingly, a first object of the present invention is to provide a light metal alloy injection-molded material having a primary α phase of magnesium that improves plastic workability, a method for producing the same, and a light alloy forged product.
A second object of the present invention is to provide a light metal alloy injection-molded material that can improve plastic workability by homogenization heat treatment, a method for producing the same, and a light alloy forged product.
[0005]
[Means for solving problems]
In order to achieve the above object, the present invention is a semi-molten state in which a solid metal / liquid phase coexists with a light metal alloy containing at least 5% by mass of aluminum as an alloy component and having a solid phase ratio After making into a semi-molten state of 70% or less , injection molding is performed to obtain a molded product having an average crystal grain size of 200 μm or less and a magnesium primary crystal α phase of 120 μm or less , and the molded product is 300 to 500 ° C. × 30 minutes to A light metal alloy forged product characterized by subjecting a MgAl compound present at the grain boundary of an injection molded product to a solid solution by subjecting it to a homogenization heat treatment within a range of 10 hours, and subjecting the injection molded product to a forging process. The manufacturing method of this is provided.
In order to generate the primary α phase of magnesium, it is necessary to perform injection molding based on a semi-melt injection molding method. Here, the injection molding by the semi-melt injection molding method refers to injection molding after a semi-molten state in which a solid phase / liquid phase coexist.
[0006]
When the base material is magnesium, it is preferable that the alloy component contains at least 5% by mass of aluminum and has an average crystal grain size of 200 μm or less.
This is because when the aluminum content is less than 5% by mass , a predetermined mechanical strength cannot be obtained. Therefore, preferred magnesium alloys in the present invention include Mg-Al-Zn alloys such as ASTM standards AZ61, AZ80, and AZ91. Further, if the average crystal grain size is 200 μm or more, the limit upsetting rate during forging, which is one of plastic workability, is 50% or less.
[0007]
In particular, an injection molding material in which the magnesium primary crystal α phase has a particle size of 120 μm or less and is substantially formed by dissolving a MgAl compound in a base material by homogenization heat treatment cannot be obtained by a conventional melt casting method. The improvement of the property is recognized (see FIG. 1), the injection molded material can be directly subjected to forging, and the process leading to forging can be simplified.
[0009]
The method of the present invention is particularly effective when the light metal alloy is made of magnesium as a base material and contains at least 5% by mass of aluminum as an alloy component, and is injection-molded in a semi-molten state with a solid phase ratio of 70% or less. Then, the magnesium primary crystal α phase has a particle size of 120 μm or less, and a homogenization heat treatment effect is exhibited (see FIG. 1).
[0010]
The conditions for the homogenization heat treatment are selected within a range of 300 to 500 ° C. × 30 minutes to 10 hours, which is sufficient to cause the MgAl compound present at the grain boundaries of the injection molded product to be dissolved in the base material. That is, the particle size and the amount (related to alloy components) of the MgAl compound, the mass of the molded product, and the like should be considered.
[0011]
Since the light metal alloy injection-molded material obtained by the present invention has a formability with a limit upsetting rate of 60% or more, a light alloy forged product can be produced by directly performing a forging process.
[0012]
DETAILED DESCRIPTION OF THE INVENTION
Hereinafter, embodiments of the present invention will be described with reference to the drawings.
A magnesium alloy of AZ80 having the following composition was prepared and injection molded under the following conditions using a semi-melt injection molding machine (model: JLM-450E, manufactured by Nippon Steel Works, Ltd.) shown in FIG. This injection molding machine heats the alloy in a screw extruder to a temperature above the solidus temperature of the molding material and below the liquidus temperature to bring it into a semi-molten state, and into the mold cavity by a high-speed injection mechanism. It is something to be shot.
[0013]
[Table 1]
Magnesium alloy composition
(Unit:% by mass )
Al Zn Mn Fe Si Cu Ni Ni Mg
Alloy A 8.1 0.45 0.27 0.0018 0.03 0.0025 0.0009 Bal.
[0014]
[Table 2]
The magnesium alloy was cut into chips and put into a hopper, and the solid fraction (solid phase / liquid phase) was adjusted by the heating temperature in the cylinder.
The success or failure of the primary α phase of the injection molded product at various solid phase ratios was confirmed by micrographs and the average particle size was measured. The results are as shown in Table 3 below.
[0016]
Further, the material as it was injection-molded and the material that was air-cooled after homogenization heat treatment (400 ° C. × 180 minutes) were tested by the following forging formability evaluation method. As a result, the primary α phase is 120 μm or less when the solid phase ratio is 70% or less, and the particle size of the primary α phase decreases as the solid phase ratio decreases, but almost no improvement in moldability is observed. However, it was found that the effect of homogenization heat treatment was exhibited from the primary crystal α phase of 120 μm or less, and the improvement was remarkable as the particle size of the primary crystal α phase became smaller.
As the forge formability evaluation method, a method was used in which evaluation was performed based on a limit upsetting rate obtained by an upsetting test using a cylindrical test piece. That is, a cylindrical test piece having a diameter of 16 mm and a height of 24 mm is forged in the height direction, and the height H when the test piece is cracked is measured, and the following formula (I)
[Expression 1]
Limit upsetting rate (%) = ((24−H) / 24) × 100 (I)
The limit upsetting rate was calculated and evaluated.
[0017]
[Table 3]
[0018]
A graph of the above results is shown in FIG. Further, the change in formability before and after the homogenization heat treatment is as shown in FIG. 2 when comparing the case where the solid fraction is 10% and 70% and the case where a magnesium alloy having the same composition is continuously cast. That is, since the presence of the primary α phase is not observed except in the present invention, the effect of the homogenization heat treatment is not recognized. Even in the present invention, the effect of the homogenization heat treatment begins to be exhibited at a solid phase ratio of 70% or less. It can be seen that the grain size of the primary crystal α phase is decreased, and the moldability is gradually improved.
[0019]
Semi-molten injection molding material A (FIG. 4) injection-molded at a solid phase rate of 10% using the above magnesium alloy, semi-molten injection molding material B (FIG. 5) injection-molded at a solid phase rate of 70%, and C when die-casting Comparing (FIG. 6) and D (FIG. 7) in the case of mold casting (continuous casting), the first two cases show the primary α phase, but the second two show the primary α phase. Absent.
[0020]
In the semi-molten injection molding materials A and B, the Mg 17 Al 12 compound existing at the grain boundary is almost dissolved and disappears by a relatively short homogenization heat treatment at 400 ° C. for 3 hours (see FIGS. 8 and 9). On the other hand, in the case of the die casting material D, even if it is subjected to a homogenization heat treatment at 400 ° C. for 6 hours, it hardly dissolves (see FIG. 10). This result appears in the presence or absence of improvement in the formability of the homogenization heat treatment.
[0021]
As described above, various effects have been confirmed for the AZ80 magnesium alloy. This primary crystal α phase of magnesium is crystallized as long as a light alloy containing magnesium and aluminum is injection-molded by a semi-melt injection molding method. In addition, as long as a light metal alloy containing magnesium and aluminum is melt-cast, the Mg 17 Al 12 compound existing at the grain boundary is precipitated. Therefore, the method of the present invention is widely applicable to light metal alloys containing magnesium and aluminum.
[0022]
【The invention's effect】
As described above, according to the present invention, in a light alloy containing at least magnesium and aluminum, the primary crystal α phase of magnesium is present by injection molding and exhibits excellent formability compared to continuous casting. In particular, when the primary crystal α phase is 120 μm or less, the Mg 17 Al 12 compound precipitated at the grain boundaries dissolves and disappears in the base material by the homogenization heat treatment, and thus more excellent moldability is exhibited.
By using such an injection-molded material of the present invention, forging is facilitated, and a magnesium alloy forged product can be provided.
[Brief description of the drawings]
FIG. 1 is a graph showing the relationship between the solid phase ratio, the average particle diameter of primary α phase, and the formability before and after homogenization heat treatment in semi-melt injection molding of AZ80 magnesium alloy.
FIG. 2 is a graph comparing the effect on formability before and after homogenization heat treatment according to the present invention and the effect on formability before and after homogenization heat treatment in continuous casting.
FIG. 3 is a schematic view of a semi-melt molding machine used in the present invention.
FIG. 4 is a photomicrograph showing the structure of a semi-molten injection molded material A injection molded at a solid phase rate of 10%.
FIG. 5 is a photomicrograph showing the structure of a semi-molten injection molded material B injection molded at a solid phase ratio of 70%.
FIG. 6 is a photomicrograph showing the structure of a die-cast material of AZ80 magnesium alloy.
FIG. 7 is a photomicrograph showing the structure of an AZ80 magnesium alloy mold casting.
8 is a photomicrograph showing the structure after homogenization heat treatment of the semi-molten injection molded material shown in FIG.
9 is a photomicrograph showing the structure after homogenization heat treatment of the semi-molten injection molded material shown in FIG.
10 is a photomicrograph showing the structure after the homogenization heat treatment of the semi-molten injection molded material shown in FIG.
Claims (1)
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| JP26388897A JP3834957B2 (en) | 1997-09-29 | 1997-09-29 | Manufacturing method of light metal alloy forged products |
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| JP26388897A JP3834957B2 (en) | 1997-09-29 | 1997-09-29 | Manufacturing method of light metal alloy forged products |
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| JPH11100632A JPH11100632A (en) | 1999-04-13 |
| JP3834957B2 true JP3834957B2 (en) | 2006-10-18 |
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