JPH10502705A - Hot chamber castable zinc alloy - Google Patents
Hot chamber castable zinc alloyInfo
- Publication number
- JPH10502705A JPH10502705A JP8504711A JP50471196A JPH10502705A JP H10502705 A JPH10502705 A JP H10502705A JP 8504711 A JP8504711 A JP 8504711A JP 50471196 A JP50471196 A JP 50471196A JP H10502705 A JPH10502705 A JP H10502705A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- zinc
- weight
- casting
- under pressure
- 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.)
- Granted
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Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C18/00—Alloys based on zinc
- C22C18/04—Alloys based on zinc with aluminium as the next major constituent
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
- Continuous Casting (AREA)
- Forging (AREA)
- Ceramic Products (AREA)
- Molds, Cores, And Manufacturing Methods Thereof (AREA)
- Supercharger (AREA)
- Refinement Of Pig-Iron, Manufacture Of Cast Iron, And Steel Manufacture Other Than In Revolving Furnaces (AREA)
- Ink Jet (AREA)
- Conductive Materials (AREA)
- Mold Materials And Core Materials (AREA)
- Sliding-Contact Bearings (AREA)
- Cylinder Crankcases Of Internal Combustion Engines (AREA)
- Vertical, Hearth, Or Arc Furnaces (AREA)
- Adornments (AREA)
- Superconductors And Manufacturing Methods Therefor (AREA)
- Casting Support Devices, Ladles, And Melt Control Thereby (AREA)
- Cooling Or The Like Of Semiconductors Or Solid State Devices (AREA)
Abstract
Description
【発明の詳細な説明】 ホットチャンバーキャスタブル亜鉛合金 本発明は、ホットチャンバー機(hot-chamber machine)において加圧下で鋳造 され得る、AlおよびCuを含有する亜鉛をベースとする合金に関するものであ る。 そのような合金は文献「SAEテクニカル・ペーパー・シリーズ930788 ,ACuZinc:金型鋳造への使用のための改良された亜鉛合金,M.D.ハ ンナおよびM.S.ラシッド,国際会議および展示会デトロイト,ミシガン,1 993年3月1−5日」に記載されている。この公知の合金は、「ACuZin c5」と呼ばれ、Cu5.0−6.0%、Al2.8−3.3%およびMg0. 025−0.05%、残部亜鉛からなる(本明細書において全ての%は重量%で ある)。この合金のクリープ耐性は、長い間ホットチャンバー内で鋳造されてき たザマク(Zamak)またはZA合金のクリープ耐性に比べ実質的に優れているが、 依然として比較的低い。 本発明の目的は上記公知の合金に比べ、より良好なクリープ耐性を有する最初 に記載したような合金を提供することである。 このために、本発明によると合金は、重量%で:Al15−20、Cu8−1 0、Si0.01−2、Mg0−0.1、Ti0−0.5、Cr0−0.5、M n0−1、Nb0−0.5および希土類金属1種または金属混合物0−0.1( この組成は以下、バリアント Iと呼ばれる)または Al25−30、Cu15−20、Si0.01−2、Mg0−0.1、Ti0 −0.5、Cr0−0.5、Mn0−1、Nb0−0.5および希土類金属1種 または金属混合物0−0.1(この組成は以下、バリアントIIと呼ばれる)の いずれかを含有し、 残部は亜鉛と亜鉛および上記合金化元素中に不可避に存在する不純物である。 実際に、一方では、460℃を越えない温度で液体状態にある2種類のバリア ントはホットチャンバー内で鋳造され得るような鋼に近似する低い攻撃性(aggre ssivity)を有すること、および他方では、鋳造状態において、バリアントIが良 好なクリープ耐性および優れた引張強さを示し、鋳造状態において、バリアント IIが優れたクリープ耐性および良好な引張強さを示すことが見出されている。 上に記載したAlおよびCu含量は固守されなければならず、さもなければ、合 金の融点は450℃より上昇し、その結果、合金は、鋳造装置に対する腐食性が 460℃以上であまりにも大きくなるので、ホットチャンバー内でもはや鋳造さ れ得ない。ケイ素含量が0.01%より少ない場合、引張強さおよびクリープ耐 性は悪化する。2%より多いケイ素含量は溶融状態で合金をあまりにペースト状 にし、そしてあまりに腐食性にする。 以下の合金が既に記載されていることをここで報告す ることは適当である: (a)17−19 Al,4.5−5.5 Cu,0.9−1.3 Si,0. 8−1.2 Mg,残部Zn(CS−A−135802) (b)28.6 Al,3.1 Cu,1 Si,0.1 Ca,0.2 Ni ,残部Zn(GB−A−769483) (c)20−40 Al,0−5 Cu,0−1 Si,0−0. 1 Mg, 0.25−2 少なくとも1種の希土類金属,残部Zn(US−A−47895 22) (d)55 Al,8 Cu,6.5 Si,4.5Be,0.12 Ni,0 .6 Ca,残部Zn(US−A−287008)。 これらの公知合金の中で、合金(a)および(c)が本発明に係る合金に最も近 接している。合金(a)はホットチャンバー内で鋳造し得るにはあまりにも低い Cu含量を有し、かつ、あまりにも高いMg含量を有する。合金(c)はまた、 あまりに低いCu含量を有し、さらに酸化された状態でさえも、酸素に対する希 土類金属の高い親和性の故に、これら希土類金属を0.25−2%含有する合金 を調製することは極端に困難である。 バリアントIは有利にはAlを15−18%、好ましくは15−17%含有す る。バリアントIIの好ましいAlおよびCu含量はそれぞれ25.5−28. 5%および15−18%である。両方のバリアントの好ましい Si含量は0.1−1%である。両方のバリアントは、 −必要であるならば粒間耐蝕性を改良するためにMgを0.1%まで; −必要であるならば延性を改良するためにTiを0.5%まで、Crを0.5% まで、そしてMnを1%まで; −必要であるならば外部腐食性に対する耐性を改良するために、すなわち白色塩 の形成を遅延させるためにNbを0.5%まで;および −必要であるならば溶融状態にある合金の表面張力を低下させるために希土類金 属または金属混合物を0.1%まで、含有してもよい。 0.1%より多いMg含量により、合金は溶融状態においてペースト状になり 、そして固体状態で脆性になる。合金はまた、Ti、CrおよびMnに対する上 記範囲から逸脱するならば、ペースト状になる。0.5%より多いNb含量およ び0.1%より多い希土類金属含量は、酸素に対するそれらの元素の高い親和性 の故に使用が困難である。 合金を調製するために用いられるZn、AlおよびCuはそれぞれ純度≧99 .99%、≧99.95%および≧99.99%を有することが望ましい。これ は合金中に不純物が存在すると流動性および機械的特性に悪影響を及ぼすことが 見出されているからである。純度・99.995%の亜鉛および純度・99.9 7%のアルミニウムが使用されることが好ましい。 合金が酸素に対する非常に高い親和性を有する金属、例えばY等を含有する場 合、該金属の少なくとも一部は酸化された状態で存在してもよい。 本発明に係る合金のバリアントIの良好なクリープ耐性およびバリアントII の優れたクリープ耐性は、下に記載される一連の比較試験により説明され、その 結果は添付の図面に示されている。 2種類の公知合金、ザマク5およびACuZinc5が本発明に係る2種類の 合金、以下「X27」と記載されるバリアントIに相当する第1の合金および以 下「X28」と記載されるバリアントIIに相当する第2の合金と一緒に試験さ れた。 これらの合金の組成は以下のとおりである: −ザマク5:4%Al,1%Cu,0.04%Mg,残部Zn; −ACuZinc5:3%Al,5.5%Cu,0.04%Mg,残部Zn; −X27:17%Al,9.5%Cu,0.5%Si,残部Zn; −X28:27%Al,16.5%Cu,0.1%Si,残部Zn。 これらの合金の試験片はホットチャンバー機において鋳造された。 一般的な鋳造条件は以下のとおりであった: −サイクル時間:12秒 −浴温度:420−460℃ −金属に加えた圧力:50MPa −ピストン速度:1.2m/s −ノズルの直径:9.5mm −型温度:180−250℃。 これら試験片の形状および寸法は亜鉛および亜鉛合金から製造されるシートお よび箔に対する引張試験において使用される試験片のための欧州亜鉛処理技術委 員会により規定されたものである。 試験片は40MPaの荷重下100℃でクリープ試験に供された。時間(単位 ,時間)の関数として測定された伸び(単位,%)を示すクリープ曲線は添付の 図面に示されている。 本発明に係る合金、特にバリアントIIに係る合金が公知合金に比べより良好 にクリープに耐性であることが示されている。 本発明に係る合金のバリアントIの優れた引張強さおよび非常に高い硬度なら びにバリアントIIの良好な引張強さおよび適度な硬度は下の表にまとめられた データにより示される。 引張試験は、上記のように製造された厚さ3mmの試験片に対し引張速度1c m/分で室温にて行われた。 本発明はまた、ホットチャンバー機内で加圧下鋳造することにより、Alおよ びCuを含有する亜鉛がベースの合金からなる物品の製造方法に関し、該方法は 上記合金が本発明の合金であり、そして上記鋳造が460℃に等しいか、または それより低い温度で行われることを特徴とする。 本発明の合金はホットチャンバーにおいて鋳造され得るが、それは必要に応じ 、コールドチャンバーにおいて、および大気圧下で鋳造され得る。 それ故に、本発明はコールドチャンバー機内で加圧下鋳造するか、または重力 鋳造することにより、AlおよびCuを含有する亜鉛がベースの合金からなる物 品の製造方法に関し、該方法は上記合金が本発明の合金であることを特徴とする 。 本発明はさらに、摩擦防止材料として本発明に係る合金を使用する方法に関す る。The present invention relates to a zinc-based alloy containing Al and Cu that can be cast under pressure in a hot-chamber machine. Such alloys are described in the document SAE Technical Paper Series 930788, ACuZinc: An Improved Zinc Alloy for Use in Mold Casting, MD Hannah and MS Rashid, International Conference and Exhibition Detroit. , Michigan, March 1-5, 1995 ". This known alloy is called "ACuZinc5" and contains 5.0-6.0% Cu, 2.8-3.3% Al and 0.5% Mg. 025-0.05%, with the balance being zinc (all percentages herein are% by weight). The creep resistance of this alloy is substantially better than the creep resistance of Zamak or ZA alloys that have been cast in hot chambers for a long time, but is still relatively low. It is an object of the present invention to provide an alloy as described above which has a better creep resistance than the known alloys described above. To this end, according to the invention, the alloys are in weight%: Al15-20, Cu8-10, Si0.01-2, Mg0-0.1, Ti0-0.5, Cr0-0.5, Mn0. -1, Nb0-0.5 and one rare earth metal or metal mixture 0-0.1 (this composition is hereinafter referred to as variant I) or Al25-30, Cu15-20, Si0.01-2, Mg0-0 0.1, Ti0-0.5, Cr0-0.5, Mn0-1, Nb0-0.5 and any one of rare earth metals or metal mixtures 0-0.1 (this composition is hereinafter referred to as variant II) The balance is zinc and zinc and impurities unavoidably present in the alloying elements. Indeed, on the one hand, the two variants in the liquid state at a temperature not exceeding 460 ° C. have a low aggressiveness approaching steel, such as can be cast in a hot chamber, and, on the other hand, In the cast state, variant I has been found to exhibit good creep resistance and excellent tensile strength, and in the cast state, variant II has excellent creep resistance and good tensile strength. The Al and Cu contents described above must be adhered to, otherwise the melting point of the alloy rises above 450 ° C., so that the alloy becomes too corrosive to casting equipment above 460 ° C. So it can no longer be cast in a hot chamber. If the silicon content is less than 0.01%, the tensile strength and creep resistance deteriorate. A silicon content of more than 2% makes the alloy too pasty and too corrosive in the molten state. It is appropriate to report here that the following alloys have already been described: (a) 17-19 Al, 4.5-5.5 Cu, 0.9-1.3 Si, 0. 8-1.2 Mg, balance Zn (CS-A-135802) (b) 28.6 Al, 3.1 Cu, 1 Si, 0.1 Ca, 0.2 Ni, balance Zn (GB-A-768483) ) (C) 20-40 Al, 0-5 Cu, 0-1 Si, 0-0. 1 Mg, 0.25-2 At least one rare earth metal, balance Zn (US-A-4789522) (d) 55 Al, 8 Cu, 6.5 Si, 4.5 Be, 0.12 Ni, 0. 6 Ca, balance Zn (US-A-287008). Of these known alloys, alloys (a) and (c) are closest to the alloy according to the invention. Alloy (a) has a Cu content that is too low to be castable in a hot chamber and a Mg content that is too high. Alloy (c) also has an extremely low Cu content and, even in the oxidized state, prepares alloys containing 0.25-2% of these rare earth metals due to the high affinity of the rare earth metals for oxygen. It is extremely difficult to do. Variant I advantageously contains 15-18% Al, preferably 15-17%. The preferred Al and Cu contents of variant II are 25.5-28. 5% and 15-18%. The preferred Si content of both variants is 0.1-1%. Both variants:-up to 0.1% Mg, if necessary, to improve intergranular corrosion resistance;-up to 0.5% Ti, if necessary, to improve ductility. Up to 0.5% and Mn up to 1%;-if necessary, to improve the resistance to external corrosivity, ie up to 0.5% Nb to delay the formation of white salts; and If necessary, rare earth metals or metal mixtures may be included up to 0.1% to reduce the surface tension of the alloy in the molten state. With an Mg content of more than 0.1%, the alloy becomes pasty in the molten state and brittle in the solid state. The alloy also becomes a paste if it deviates from the above ranges for Ti, Cr and Mn. Nb contents greater than 0.5% and rare earth metal contents greater than 0.1% are difficult to use due to the high affinity of those elements for oxygen. The Zn, Al and Cu used to prepare the alloy each have a purity ≧ 99. It is desirable to have 99%, ≧ 99.95% and ≧ 99.99%. This is because the presence of impurities in the alloy has been found to adversely affect fluidity and mechanical properties. Preference is given to using zinc with a purity of 99.995% and aluminum with a purity of 99.97%. If the alloy contains a metal with a very high affinity for oxygen, such as Y, at least some of the metal may be present in an oxidized state. The good creep resistance of variant I of the alloy according to the invention and the excellent creep resistance of variant II are illustrated by a series of comparative tests described below, the results of which are shown in the accompanying drawings. Two known alloys, Zamak 5 and ACuZinc5, correspond to two alloys according to the invention, a first alloy corresponding to variant I, hereinafter referred to as "X27", and a variant II, hereinafter referred to as "X28" Was tested with a second alloy. The composition of these alloys is as follows:-Zamak 5: 4% Al, 1% Cu, 0.04% Mg, balance Zn;-ACuZinc 5: 3% Al, 5.5% Cu, 0.04% -X27: 17% Al, 9.5% Cu, 0.5% Si, balance Zn; -X28: 27% Al, 16.5% Cu, 0.1% Si, balance Zn. Specimens of these alloys were cast in a hot chamber machine. The general casting conditions were as follows:-Cycle time: 12 seconds-Bath temperature: 420-460 ° C-Pressure applied to the metal: 50 MPa-Piston speed: 1.2 m / s-Nozzle diameter: 9 0.5 mm-Mold temperature: 180-250 ° C. The shape and dimensions of these specimens are those specified by the European Zinc Processing Technical Committee for specimens used in tensile tests on sheets and foils made from zinc and zinc alloys. The specimen was subjected to a creep test at 100 ° C. under a load of 40 MPa. A creep curve showing the elongation (unit,%) measured as a function of time (unit, time) is shown in the accompanying drawings. It has been shown that the alloy according to the invention, in particular the variant II, is better resistant to creep than the known alloys. The excellent tensile strength and very high hardness of variant I and the good tensile strength and moderate hardness of variant II of the alloy according to the invention are shown by the data summarized in the table below. The tensile test was performed on a test piece having a thickness of 3 mm manufactured as described above at a tensile speed of 1 cm / min at room temperature. The present invention also relates to a method for producing an article comprising a zinc-based alloy containing Al and Cu by casting under pressure in a hot chamber machine, wherein said alloy is an alloy of the present invention; The casting is performed at a temperature equal to or less than 460 ° C. While the alloy of the present invention may be cast in a hot chamber, it may optionally be cast in a cold chamber and under atmospheric pressure. Therefore, the present invention relates to a method for producing an article comprising a zinc-based alloy containing Al and Cu by casting under pressure in a cold chamber machine or by gravity casting, wherein said alloy comprises Characterized in that it is an alloy of The invention further relates to a method of using the alloy according to the invention as an anti-friction material.
───────────────────────────────────────────────────── フロントページの続き (81)指定国 EP(AT,BE,CH,DE, DK,ES,FR,GB,GR,IE,IT,LU,M C,NL,PT,SE),OA(BF,BJ,CF,CG ,CI,CM,GA,GN,ML,MR,NE,SN, TD,TG),AP(KE,MW,SD,SZ,UG), AM,AU,BB,BG,BR,BY,CA,CN,C Z,EE,FI,GE,HU,IS,JP,KG,KP ,KR,KZ,LK,LR,LT,LV,MD,MG, MN,MX,NO,NZ,PL,RO,RU,SG,S I,SK,TJ,TM,TT,UA,US,UZ,VN────────────────────────────────────────────────── ─── Continuation of front page (81) Designated countries EP (AT, BE, CH, DE, DK, ES, FR, GB, GR, IE, IT, LU, M C, NL, PT, SE), OA (BF, BJ, CF, CG , CI, CM, GA, GN, ML, MR, NE, SN, TD, TG), AP (KE, MW, SD, SZ, UG), AM, AU, BB, BG, BR, BY, CA, CN, C Z, EE, FI, GE, HU, IS, JP, KG, KP , KR, KZ, LK, LR, LT, LV, MD, MG, MN, MX, NO, NZ, PL, RO, RU, SG, S I, SK, TJ, TM, TT, UA, US, UZ, VN
Claims (1)
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
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BE9400676A BE1008479A3 (en) | 1994-07-18 | 1994-07-18 | Zinc alloy castable room hot. |
BE9400676 | 1994-07-18 | ||
PCT/EP1995/002820 WO1996002682A1 (en) | 1994-07-18 | 1995-07-12 | Hot chamber castable zinc alloy |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH10502705A true JPH10502705A (en) | 1998-03-10 |
JP3800345B2 JP3800345B2 (en) | 2006-07-26 |
Family
ID=3888263
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP50471196A Expired - Fee Related JP3800345B2 (en) | 1994-07-18 | 1995-07-12 | Hot chamber castable zinc alloy |
Country Status (16)
Country | Link |
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EP (1) | EP0771365B1 (en) |
JP (1) | JP3800345B2 (en) |
KR (1) | KR100343309B1 (en) |
AT (1) | ATE173029T1 (en) |
AU (1) | AU3113995A (en) |
BE (1) | BE1008479A3 (en) |
BR (1) | BR9507577A (en) |
CA (1) | CA2185013C (en) |
CZ (1) | CZ287825B6 (en) |
DE (1) | DE69505820T2 (en) |
DK (1) | DK0771365T3 (en) |
ES (1) | ES2126301T3 (en) |
FI (1) | FI114400B (en) |
PE (1) | PE12696A1 (en) |
PL (1) | PL178557B1 (en) |
WO (1) | WO1996002682A1 (en) |
Families Citing this family (3)
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KR100961081B1 (en) * | 2009-03-03 | 2010-06-08 | 임현규 | Zinc-aluminium alloys with high strength and low density |
KR101955995B1 (en) * | 2017-03-21 | 2019-03-08 | 주식회사 지.에이.엠 | High strength aluminium-zinc alloy and high strength aluminium-zinc alloy casting |
CN112522540A (en) * | 2020-12-01 | 2021-03-19 | 江苏同生特钢制造有限公司 | Zinc alloy casting and preparation method thereof |
Family Cites Families (3)
Publication number | Priority date | Publication date | Assignee | Title |
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GB769483A (en) * | 1953-06-30 | 1957-03-06 | Willi Neu | Zinc aluminium alloy and process for the production thereof |
US2870008A (en) * | 1954-11-18 | 1959-01-20 | Main Alloy Company Establishme | Zinc-aluminium alloys and the method for producing same |
US4789522A (en) * | 1986-06-27 | 1988-12-06 | Queen's University At Kingston | Castable zinc-aluminum alloys |
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1994
- 1994-07-18 BE BE9400676A patent/BE1008479A3/en not_active IP Right Cessation
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1995
- 1995-07-12 JP JP50471196A patent/JP3800345B2/en not_active Expired - Fee Related
- 1995-07-12 CA CA002185013A patent/CA2185013C/en not_active Expired - Fee Related
- 1995-07-12 WO PCT/EP1995/002820 patent/WO1996002682A1/en active IP Right Grant
- 1995-07-12 EP EP95926933A patent/EP0771365B1/en not_active Expired - Lifetime
- 1995-07-12 AT AT95926933T patent/ATE173029T1/en not_active IP Right Cessation
- 1995-07-12 CZ CZ199751A patent/CZ287825B6/en not_active IP Right Cessation
- 1995-07-12 DE DE69505820T patent/DE69505820T2/en not_active Expired - Fee Related
- 1995-07-12 KR KR1019960705161A patent/KR100343309B1/en not_active IP Right Cessation
- 1995-07-12 BR BR9507577A patent/BR9507577A/en not_active IP Right Cessation
- 1995-07-12 DK DK95926933T patent/DK0771365T3/en active
- 1995-07-12 ES ES95926933T patent/ES2126301T3/en not_active Expired - Lifetime
- 1995-07-12 AU AU31139/95A patent/AU3113995A/en not_active Abandoned
- 1995-07-12 PL PL95318133A patent/PL178557B1/en not_active IP Right Cessation
- 1995-07-13 PE PE1995273756A patent/PE12696A1/en not_active Application Discontinuation
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1997
- 1997-01-16 FI FI970177A patent/FI114400B/en active IP Right Grant
Also Published As
Publication number | Publication date |
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ES2126301T3 (en) | 1999-03-16 |
DK0771365T3 (en) | 1999-07-19 |
PL178557B1 (en) | 2000-05-31 |
CZ287825B6 (en) | 2001-02-14 |
BR9507577A (en) | 1997-09-09 |
AU3113995A (en) | 1996-02-16 |
BE1008479A3 (en) | 1996-05-07 |
WO1996002682A1 (en) | 1996-02-01 |
FI970177A (en) | 1997-01-16 |
DE69505820T2 (en) | 1999-07-08 |
EP0771365B1 (en) | 1998-11-04 |
KR100343309B1 (en) | 2002-11-25 |
PL318133A1 (en) | 1997-05-12 |
CA2185013A1 (en) | 1996-02-01 |
JP3800345B2 (en) | 2006-07-26 |
CA2185013C (en) | 2006-08-29 |
EP0771365A1 (en) | 1997-05-07 |
DE69505820D1 (en) | 1998-12-10 |
ATE173029T1 (en) | 1998-11-15 |
FI970177A0 (en) | 1997-01-16 |
CZ5197A3 (en) | 1997-04-16 |
PE12696A1 (en) | 1996-04-23 |
FI114400B (en) | 2004-10-15 |
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