201249575 六、發明說明 【發明所屬之技術領域】 !· 發明領域 本發明涉及彌散強化鉑基合金，並且更具體地說，涉 及—用於焊接該等合金的方法。 【先前技術】 2· 習知技術說明 由貴重金屬和貴重金屬合金例如較佳的是PGM材料 組成的結構零件被用於玻璃行業，特別是特種玻璃熔化和 熱成型工廠。該等用於熔合技術也稱爲PGM (鉑族金 屬）產品的工廠部件用來熔化、精煉、運輸、均質化並分 配該液體玻璃。該等貴重金屬合金大多是合金添加鍺、銥 或金的鉑基合金。如果由於玻璃熔體施加的機械和/或熱 應力而要求非常高的結構零件強度，則越來越多地使用氧 化物彌散強化鈾基合金，因爲該等鉑基合金的特徵在於具 有比標準合金更高的經受熱、機械和化學應力的能力。氧 化物彌散合金（下文中也稱爲ODS合金）不同之處在於 一非常均勻的微觀結構。 帶有玻璃熔體的工廠零件往往是被設計成薄壁管道系 統的貴重金屬板結構。熔融玻璃在1 000°C和1700°C之間 的溫度下流過該等零件。 由於PGM (鉑族金屬）材料的高熔點，它們的不同 之處在於耐高溫性，此外，在於高機械強度和耐磨損性， -5- 201249575 並且因此尤其適用於生產設備中的結構零件或者與該玻璃 熔體接觸的設備零件。合適的材料爲鈾以及鉑和/或其他 PGM金屬的合金，該等材料還可任選地包含少量基本金 屬作爲另外合金組分或氧化性添加劑。典型材料爲精煉 鉛、鉑铑合金以及鉑銥合金，它們含有少量的細分散的耐 火金屬氧化物，例如特別是二氧化锆或氧化釔，以提高強 度和耐高溫蠕變性。 然而，除了選擇該合適材料之外，該等貴重金屬部件 的生產，特別是成形在確定強度中也發揮了重要作用。通 常，來自單獨金屬板的該等部件連接在一起，以提供所要 求的幾何形狀，並且通常藉由熔體焊接相互連接》在這個 過程中，藉由供熱將有待相互連接的所述金屬板之間的接 點轉化成熔融狀態，適當時，還將一相同類型的塡充材料 轉化成熔融狀態並且熔合在一起。在這種情況下，可由一 電弧或一點燃氣體-氧氣混合物生成熔合熱。然而，如果 以這種方式連接的部件暴露于非常高的溫度，例如 1 2 00°C以上，焊縫常形成整體材料黏結的弱點。已確定 的原因係該焊縫中的不均勻性以及在熱影響區內該微觀結 構的變化。特別是圓柱形結構零件例如管道中的縱向焊縫 由於作用應力而具有特定風險，該等作用應力幾乎是圓周 焊縫的兩倍高，並且因此該等縱向焊縫往往不合格並且裂 開。當使用已知的焊接工藝例如鎢極惰性氣體（TIG )焊 接、電漿焊接、鐳射或自熔焊接時，該合金被熔化《«但是 在1 200°C以上使用過程中，當由於重結晶而熔化經典的 201249575 置換固溶體合金時，在該焊縫中僅可觀察到很小的強度損 失，焊接氧化物彌散強化合金時的熔化導致該熔體中通常 爲Zr02和/或Υ2〇3的大部分彌散體凝結和漂浮。在該焊 縫中形成一粗粒化的凝固微觀結構。因此’該焊縫中所述 彌散體的強化作用無效。然後’一種以這種方式連接在一 起的部件的應力承受能力及其使用壽命降低至來自標準合 金的相連部件的水平。 用於防止這種缺點的措施從 JP 5 2 1 2 5 77 Α和 ΕΡ 03 20877 B1中已知的。在本申請揭露的方法中，ODS金 屬板上的一熔合焊縫隨後用一種Pt-ODS箔覆蓋，並且藉 由高溫下錘擊而壓製成該縫。這種措施藉由該箔提高了該 焊縫的粒徑分佈細度，並且從而降低了表面上裂縫形成的 可能性。除了另外過時的替代方案之外，已求助於依靠錘 擊焊縫形成的整體接頭。然而，這種類型的接頭質量受到 很大變化。爲了消除該等變化，需要極大的費用來製備該 焊縫並在焊接過程中要求非常精確地控制工藝參數。在這 個過程的情況下，證明在錘擊期間均勻加熱兩種有待連接 的材料，特別是金屬板係非常困難的。這樣做的時候，往 往幾乎不可能用炬在焊接位置充分加熱較低金屬板，以在 錘擊過程中獲得一良好的黏結效果。因此該過程係非常艱 苦的’不必然地導致一最佳結果，並且是非常昂貴的。此 外’製造錘擊焊縫時有一根本問題，因爲在鍺含量大於 4% (按重量計）的合金的情況下並且通常在0DS合金的 情況下’在錘擊過程中該材料具有低的黏合傾向。已經存 201249575 在於該ODS材料中的氧化物和/或在錘擊過程中形成的所 述氧化物，主要是氧化铑，顯著降低了所述兩個結構零 件，特別是金屬板的黏結。所述不良黏結具有顯著增加生 產支出的效果，但是同時也有增加該縫中連接區域的某些 區域內不再獲得充分黏結的風險的效果。 在DE 1 023 7763 B4中，在生產氧化物彌散（ODS) 金屬材料結構零件的永久整體接頭過程中，該等單獨材料 的焊接在其熔化溫度以下分別進行，其中在該連接區域內 至少部分形成一擴散黏結。在一第二個工藝步驟中，將該 擴散黏結，較佳的是整個連接區域被加熱到同樣低於有待 相互連接的材料和/或結構零件的熔化溫度的溫度，並且 在此溫度下機械地再壓實，較佳的是錘擊。在焊接操作前 根據彼此之間的安排，在這種情況下有待相互連接的這兩 種材料限定了該等連接，後者通常也形成該連接區域，即 其中即將生產所希望的這兩種材料之間的接頭的區域。在 這個過程中，藉由安排用於生產一即將在加熱下機械再壓 實前進行的擴散焊接黏結，從而提供氧化物彌散（ODS ) 金屬材料結構零件的永久性的整體接頭。一較佳實施方式 提供了使用一焊接塡料。將該焊接塡料安排在有待相互連 接的氧化物彌散金屬材料的這兩種材料和/或結構零件之 間的連接區域內。這裡，該焊接塡料可以爲一分開的元件 或至少一個該連接區域中彼此相對的連接面上的一塗料。 具體地，在這種情況下合適的焊接塡料爲易延展的熔合合 金’例如PtAu5、Ptlrl、純Pt，但還有更堅固的合金，例 -8- 201249575 如PtRh5、PtRhlO、Ptlr3。所述文件強調，由於所述兩種 材料之間的黏合傾向大幅增加，該焊接塡料可以實現一有 待相互連接的這兩種材料之間顯著改善的黏結，並且這進 而大大降低了生產費用。此外，所述連接區域承受熱和機 械應力的能力應該會顯著提高。另外，所述文件強調尤其 佳的是***一貴重金屬箔。在一較佳實施方式中，該文件 傳授了，將該等有待連接的所述金屬板的邊緣進行倒角， 置於彼此上方，其中該等倒角的邊緣精確地在彼此之上， 並且在一冰凍步驟中，首先與一擴散黏結暫時連接，該擴 散黏結機械地再壓實以在一後續步驟中實現最終擴散黏 結。 缺點係該等邊緣的倒角的部分彼此面對並且精確地重 疊’尤其是在施加機械負荷時，這將導致一種比另一金屬 板薄的擴散黏結或者一更低強度的擴散黏結，兩者均導致 該黏結的強度更低。此外，使用與有待連接的所述金屬板 不同的組分的焊接塡料或箔是不利的，因爲產生的柯肯達 爾效應（Kirkendall-Effect)將導致孔隙形成，從而消弱 了該等邊緣之間的焊接接頭。 【發明內容】 本發明係基於提供一用於連接氧化物彌散貴重金屬板 @改進方法以及一用於實施該方法的裝置的目的。 發明簡要說明 -9 - 201249575 本發明涉及一種按照下列各項製備焊接物品之方法： 1. 一種用於生產彌散強化鉑基合金板材的焊接物品 之方法，包括以下步驟 提供至少一塊彌散強化鉑基合金板材； 將所述彌散強化鈾基合金板材的有待焊接連接的邊緣 進行倒角： 將該等有待焊接連接的倒角的邊緣進行重疊； 將所述彌散強化鉑基合金的重疊的倒角的邊緣僅在所 述邊緣的周邊進行熔體焊接； 將該鉑板材利用一壓焊方法進行焊接連以生產該焊 縫，該壓焊方法選自錘焊、噴九加工、輥式縫焊接、電阻 焊接、擴散焊接、摩擦焊接及其組合； 將該焊接物品周邊上的熔體焊接部分去除》 2- 如項1所述之方法，其中該熔體焊接步驟爲TIG 焊接（鎢極惰性氣體焊接），該TIG焊接包括以下步驟： a.調節TIG焊接電源，以使輸入到該焊縫中的能量減到 最少；b.將所述焊縫與一電弧氣體組合物接觸，以最大 限度地快速淬火該焊縫；c.將所述焊縫與一第二氣體接 觸，該接觸主要在所述焊縫的底面處，以便將該焊縫的底 面淬火；d.將所述焊縫與一尾部氣體（trailing gas)接 觸，以增強該焊縫的冷卻從而超越由所述電弧氣體和所述 第二氣體實現的冷卻。 3. 如項1或2所述之方法，該焊接物品係一管狀物 件，並且該等有待連接的邊緣屬於相同的鉑基合金材料 -10- 201249575 板。 4. 如項1至3中任一項所述之方法，其中所述鉑基 合金具有一組分，該組分主要由金、銥或铑組成，特別是 由選自 PtAu5、Ptlr 1、PtRh5、PtRhl 0、PtRh20、Ptlr3、 Ptlr5純鈾及其組合的合金組成。 5. 如項1至4中任一項所述之方法，該鈾基合金係 用一種氧化物進行氧化物彌散強化的，所述氧化物係來自 由氧化釔、二氧化锆及其混合物組成的組。 6. 如項1至5中任一項所述之方法，該鉑基合金具 有 PtAu5、Ptlrl、PtRh5、PtRhlO、Ptlr5 或 Ptlr3 的組 分，並且是用氧化釔或二氧化锆進行氧化物彌散的。 7. 如項1至6中任一項所述之方法，其中藉由切 斷、金屬剪、切割輪、線侵蝕、噴射切割、鐳射切割及其 組合實現該等熔體焊接部分的去除。 8. 如項1至7中任一項所述之方法，其中該熔體焊 接方法選自下組’該組由以下各項組成：電漿焊接、鐳射 焊接、TIG (鎢極惰性氣體）焊接、電阻焊接或自熔焊 接。 9. 如項2至8所述之方法，其中所述電源係—脈衝 逆變器。 10. 如項2至9所述之方法，其中所述電弧氣體具有 —選自下組的組成’該組由以下各項組成：氣氣、氨氣及 其混合物。 11. 如項2至1 0中任一項所述之方法，其中所述第 -11 - 201249575 二氣體係一氣體混合物。 12. 如項2至1 1中任一項所述之方法，其中所述尾 部氣體選自下組’該組由以下各項組成：氣氣、氮氣、氦 氣、二氧化碳及其混合物。 13. 如項2所述之方法，其中所述第二氣體選自下 組，該組由以下各項組成：氬氣、氮氣、氦氣、二氧化碳 及其混合物。 14. 如項2所述之方法’其中所述接點由一冷卻的夾 具保持。 15. 如項2所述之方法’其中該尾部氣體藉由一氣體 噴嘴施用，並且所述噴嘴藉由傳導淬火該焊接件。 16. 如項1所述之方法，其中所述噴九加工介質選自 下組，該組由以下各項組成：玻璃珠、陶瓷球或鋼九。 17-如項1所述之方法，其中所述噴九加工步驟進行 了範圍從大約5 sec/cm2至60 sec/cm2的時間段。 18. 如項1所述之方法，其中所述九由平均直徑範圍 爲大約0.1 mm至大約5 mm且實質上均勻、基本上爲球 形的顆粒組成。 19. 如項1所述之方法，其中所述熔體焊接僅在該板 材一側在所述邊緣周邊上進行。 20. 如項1所述之方法，其中所述熔體焊接僅在該板 材一側在所述邊緣周邊上進行，並且在相反側上所述倒角 的邊緣不重题並且彼此分開進行安排。 2 1.如項1所述之方法，其中該至少兩個金屬板部分 -12- 201249575 被安排爲重疊的，該等倒角邊緣向外延伸 屬板部分。 22·如項1所述之方法，其中該焊接 的底座上利用一壓焊方法進行，並且其中3 部分置於該底座上。 23. 如項22所述之方法，其中將 300°C 至 600°C，較佳的是 350°C 至 550。 的是 400°C 至 500。(：。 24. 如項1所述之方法，其中該等倒声 寬度（F)係原始金屬板寬度（t0)的1至 是2倍’和/或該倒角角度爲15。至27c 17,6°至25.6°’進一步較佳的是從19.6。至 佳的是大約2 1.6 °。 25. 如項1所述之方法，其中該壓焊宅 的熔體焊接部分上從該板材的一側開始進f 等邊緣繼續至該板材的相反側。 26. 如項1所述之方法，其中該壓焊名 間大約中間的一點上進行，並且沿著該等重 該板材的一側，隨後從大約中間的所述點圍 相反側。 27. —種彌散強化鉑基合金板材的焊接 物品係藉由一如項1所述之方法得到的。 【實施方式】 ，遠離該鄰近金 I接在一已預熱 g少一個金屬板 該底座預熱到 C，進一步較佳 与的邊緣的倒角 3倍，較佳的 '，較佳的是從 23.6°，並且最 E該等重疊邊緣 ί，並且沿著該 έ該板材兩側之 i戥邊緣繼續至 目始至該板材的 丨物品，該焊接 -13- 201249575 發明詳細說明 本發明提供了一用於焊接彌散強化鉑基合金的方法。 本發明的熔體焊接慣例係使得當與該基本金屬相比時，顯 著減少或消除了習知技術方法的粗糙脆性金屬間化合物特 徵的形成，並且該等特徵的形成嚴重降低了該焊接物品的 連接強度和延展性。 可以噴九加工該焊縫，以均質化該焊接件和熱影響 區。根據本發明，以一種經濟有效的方式焊接彌散強化鈾 基合金，並因此保留其有用的機械性能。 在本發明的一方面，由彌散強化鉑基合金板材生產了 —焊縫。確切地說，利用一方法焊接該合金，所述方法包 括以下步驟： 提供至少一塊彌散強化鉑基合金板材； 將所述彌散強化鉑基合金板材的有待焊接連接的邊緣 進行倒角； 將該等有待焊接連接的倒角的邊緣進行重疊； 將所述彌散強化鈾基合金的重疊的倒角的邊緣僅在所 述邊緣的週邊進行熔體焊接； 將該鉑板材利用一壓焊方法進行焊接連接以生產該焊 縫，該壓焊方法選自下組：錘焊、噴九加工、輥式縫焊 接、電阻焊接、擴散焊接、摩擦焊接及其組合； 將該焊接物品週邊上的熔體焊接部分去除。 例如’如 EP 0320877、 US-B-6511523 或 EP 1781830 中所述’可提供合適的彌散強化鉑基合金板材。在本發明 -14- 201249575 的一實施方式中，形成該鉑板材的鈾基合金具有一組分， 該組分主要由鉑連同金、銥或铑組成，尤其是由選自 PtAu5、Ptlrl、PtRh5、PtRhlO、PtRh20、Ptlr3、Ptlr5、 純鉑及其組合組成的組的合金。在另一實施方式中，更確 切地說，該鉑基合金可用一選自氧化釔、二氧化銷及其混 合物組成的組的氧化物進行氧化物彌散強化。在這方面， 上面引用的專利文獻描述了這點。取決於期望的材料性 能，這種氧化物彌散強化可存在於純鉑以及這部分中上面 揭露的所述合金中。更確切地說，該鈾基合金具有一種 PtAu5、Ptlrl、PtRh5、PtRhlO、Ptlr3、Ptlr5 的組成或者 是純鉑，並且用氧化釔或二氧化鉻進行氧化物彌散。 根據本發明的另一方面，較佳的是，特別是以一種直 線方式對所述邊緣進行倒角。這裡，當所述金屬板部分被 安排爲重疊時，將該等有待連接的金屬板部分連接，其方 式爲該等倒角的邊緣隨後向外延伸，即遠離該鄰近金屬板 部分。已經發現了以這種方式將所述金屬板部分進行倒角 和對齊提高了連接產品的蠕變斷裂強度。下面更詳細地示 出了這點。也在這種情況下，對所述金屬板部分進行擴散 錘焊。一根據本發明的較佳方法也包括上面討論的兩個方 面，即提供並且預熱一底座，並以提出的方式形成所述倒 角。 所述倒角的邊緣的倒角寬度（F)較佳的是爲原始金 屬板厚度（t0)的1至3倍，較佳的是爲2倍。進一步較 佳的是，該倒角角度α爲大約15°至大約27。，較佳的是 -15- 201249575 爲大約17.6°至大約25.6°，進一步較佳的是爲大約19.6° 至大約23.6°，並且最佳的是爲大約21.6°。較佳的是，以 這樣一方式成形所述倒角的邊緣，使得所述邊緣的倒角的 部分相互平行或至少基本上相互平行，這意味著當所述倒 角部分被安排爲彼此面對時，兩個邊緣會相互補充。當兩 個邊緣的倒角角度α相同時常常如此。 隨後將該等邊緣進行重疊。在本發明的另一實施方式 中，如圖1所描繪和以下所述，以這樣一方式進行所述邊 緣重蛵，使得當所述金屬板部分被安排爲重疊時，所述倒 角的邊緣隨後向外延伸，即遠離該鄰近的金屬板部分。在 本發明的又另一實施方式中，有待連接的所述邊緣屬於相 同的鉑基合金材料板，因此不得不彎曲該鉬材料板以允許 該等邊緣重题，這樣該焊接物品將是一管狀物件。該管狀 焊接物品的截面並沒有具體限制，例如可以是圓形、橢圓 形或多邊形。 較佳的是，該等金屬板部分被安排爲重疊，其中重疊 長度爲原始金屬板厚度（to)的2.5至7.5倍，較佳的是 爲原始金屬板厚度（t0)的4至7倍。擴散焊接後，所述 金屬板部分的重疊係原始金屬板厚度（t0)的3至8倍， 較佳的是爲原始金屬板厚度（t0)的5至7倍。 隨後將該等重疊的邊緣在所述邊緣的周邊進行熔體焊 接。在熔體焊接過程中，所述彌散體可以凝結，因此該焊 縫中所述彌散體的強化作用將會無效或至少受限制。由於 在該過程中稍後會切掉該等熔體焊接的部分，因此最終產 -16- 201249575 品的特性將不受影響。原則上，只要輸入到該鉑板材中的 能量不受限制’則用於熔體焊接的方法並不受限於一具體 方法’這樣分散體的熔化和凝固在空間上不限於進行熔體 焊接連接的區域。 所述熔體焊接方法通常可選自電漿焊接、鐳射焊接、 TIG (鎢極惰性氣體）焊接、電阻焊接或自熔焊接。技術 人員熟悉該等普通的熔體焊接方法，並且瞭解如何利用該 等熔體焊接方法實現本發明的目的。在所述邊緣周邊上的 熔體焊接可以僅在該鉑板材的其中一側或該鈾板材的兩側 進行。 顯然，將焊接頭置於該等重疊的邊緣上，這樣在這個 特定位置對該等重疊的邊緣進行焊接連接。通常，所述熔 體焊接接頭不需要具有一大的尺寸，並且一個單一焊接點 就足夠。如圖2a和2b所描繪，把焊接頭將置於有待連接 的所述邊緣的周邊，靠近該鈾板材的側面邊界。 在本發明的又另一實施方式中，有待相互連接的所述 邊緣在它們的整個長度上重疊，並且在該鉑板材的兩側面 邊界上進行熔體焊接，並且建立熔體焊接接頭。 在本發明的又另一實施方式中，僅在該板材的一側在 該等邊緣周邊上進行熔體焊接，並且在相反側上所述對角 邊緣不重疊並且被安排爲彼此分開。 在這個實施方式中，該等有待相互連接的邊緣在它們 的部分長度上重疊，並且在該舶板材的其中一側面邊界上 進行熔體焊接。在這個實施方式中，該舶板材的所述邊緣 -17- 201249575 通常在該鈾板材的一側面邊界上重疊，並且靠近該側面邊 界進行焊接連接，同時該等彼此分開的所述邊緣與各自的 側面邊界相距甚遠。在這種情況下，兩個邊緣通常隔開， 從而在所述邊緣之間形成一 V形間隙，並且在該間隙的 一側面邊界端進行重疊並部分熔體焊接連接，同時在相反 側面邊界上不存在重疊或熔體焊接接頭。 在本發明的又另一實施方式中，該等有待相互連接的 所述邊緣在它們的部分長度或它們的整個長度上重疊，並 且將在其上進行熔體焊接連接的該鉑板材的周邊置於一區 段上，該區段延伸超過剩下的鉑板材的側面邊界。換言 之，該等有待連接的邊緣上的該鉑板材比該焊接物品的其 餘部分的預期寬度更寬，以便形成一端耳（terminal ear )並在實施壓焊步驟後切掉該端耳，該端耳僅僅節省 了設置焊接頭的目的，所述熔體焊接頭與有待連接的所述 邊緣的部分空間分開。這樣，可以使正被切掉並回收的鈾 板材的數量以及同時用於這個步驟的工作時間和工作量減 到最小。圖2a中描繪了這樣一情況。 在本發明的另一實施方式中，TIG (鎢極惰性氣體） 焊接係一用於本發明目的的合適方法。更確切地說，該 TIG焊接包括以下步驟： a. 調節TIG焊接電源’以使輸入到該焊縫中的能 量減到最小； b. 將所述焊縫與一電弧氣體組合物接觸，該組合物 被調整爲最大限度地快速淬火該焊縫； -18- 201249575 C· 將所述焊縫與一第二氣體接觸，該接觸主要在所 述焊縫的底面處’以便淬火該焊縫的底面；並且 d. 將所述焊縫與一尾部氣體接觸，以增強該焊縫的 冷卻’從而超越了由所述電弧氣體和所述第二氣體實現的 冷卻》 使輸入到該焊縫中的能量減到最少的TI G焊接電源的 實例包括（但不僅限於）那些利用逆變器技術的電源，所 述逆變器技術產生提高回應速度的脈衝交流電（AC)波 形。所述脈衝逆變器電源產生一具有最小電流的高度穩定 的電弧，該最小電流由完全不同於常規交流電的方波AC 脈衝保持。這種類型的電弧對於焊接薄的鉑板是有利的， 其過程通常是艱難的，且允許高速焊接。該脈衝逆變器還 生成了一更集中的電弧，該電弧允許輸入到該焊縫中的能 量更加精確。這種特徵係控制該焊縫快速凝固性質的關 鍵》因爲從10 Hz至500 Hz的所述高速脈衝將該電弧集 中於一極細的點，所以實現了這點，同時該電弧的穩定性 提高了。最後，高脈衝速度增強了電極的清洗，從而允許 該焊縫的逆轉或清洗週期減少。這再次減少了輸入到系統 中的能量的量。 不僅將該電弧氣體混合物或各種氣體混合物控制在該 焊接電弧而且控制在該焊縫的底側並直接控制在該焊縫本 身的目的提高了該焊縫的冷卻速度，從而可在該焊縫中獲 得一快速凝固的結構。用於保護該焊縫的前面和背面的夾 具和氣體噴嘴的類型係不同·的’並且取決於有待焊接的該 19- 201249575 部件的配置以及有待形成的接頭的類型。該電弧氣體組成 係氬氣或氮氣或兩者的一混合物。用於保護並淬火該焊縫 底側的覆蓋氣體（尾部氣體）係氬氣、氮氣、氨氣或二氧 化碳或者該等氣體中的兩種或更多種的某一組合。爲了提 高該夾具的淬火速度，該夾具本身可以進行冷卻。通過該 尾部氣體噴嘴應用的覆蓋氣體係氬氣、氮氣、氦氣或二氧 化碳或者該等氣體中的兩種或更多種的某一組合。該氣體 噴嘴可與該焊接物品實體接觸，從而藉由傳導淬火該焊接 物品。 按照行業來說TIG焊接係令人滿意的，因爲它易於應 用並且廣泛實施（deployment)。因此，藉由利用一使焊 接必需的能fi減到最少的TIG電源，採用盡可能快地冷卻 該焊縫的保護氣體的一最佳組合，並且適當地緊固該接頭 以便將一淬火氣體主要用於該焊縫底側馬上拖尾該焊縫的 一點上，從而進行TIG焊接。較佳的是，由於其以高脈衝 速度形成一凝聚電弧的能力，所以利用一脈衝AC逆變器 電源，從而降低焊接所需的能量。較佳的是，所述電弧和 保護氣體選自提供所要求的最大淬火速度的氦氣、氬氣或 它們的一混合物。夾具和馬蹄形噴嘴用於優化焊接易用 性，並且它們的佈置和設計將取決於焊縫配置和部件幾何 形狀而有所不同。典型的淬火和保護氣體選自下組，該組 由以下各項組成：氬氣、氦氣、氮氣、二氧化碳及其混合 物。 隨後，利用一壓焊方法焊接連接該鉑板材以生成該焊 -20- 201249575 縫，該壓焊方法選自下組：錘焊、噴九加工、輥 接、電阻焊接、擴散焊接、摩擦焊接及其組合。 該等焊接方法係在該鉑板材的熔化溫度以下實 且爲能在幾個實驗後獲得最佳結果的技術人員熟悉 工方法。但是，較佳的是在室溫以上但是該熔化溫 的溫度下實施該等方法。可在大約1 000°C至大約 的溫度下，更確切地說大約1 200。(：至大約1 3 00°C 約1400°C至大約1 600。<：的溫度下進行這種壓焊操 一步較佳的是，在所述金屬板部分被安排爲重疊前 述金屬板部分在相互面對側上粗化，較佳的是，表 度Ra爲大約0.05 μιη至大約25 μιη，進一步較佳 大約0.5 μιη至大約10 μηι。可以已經在倒角過程 用限定的切割邊緣切斷或者藉由用未限定的切割邊 而進行隨後的表面加工如硏磨，從而提供這種粗糙 化使之有可能在擴散焊接區域提供一增大的表面寻 或使得盡可能地提高焊接參數的可控性。例如，合 熱方式係一氣氧炬。可以局部加熱該等金屬板部分 加熱有待壓焊的整個範圍係可能的，但是往往不經 於摩擦焊接，特別是摩擦攪拌焊接係一用於連接該 的合適方法。 電阻焊接提供了依靠一電流穿過該有待連接的 的邊緣而加熱該等有待連接的邊緣。在輥式接縫焊 使一輥沿著該等有待連接的邊緣通過’將鉑板材的 疊的邊緣壓緊，並因此形成一擴散黏結。同時，可 式縫焊 施的並 的冷加 度以下 1 700°C 或者大 作。進 ，使所 面粗糙 的是爲 中藉由 緣切斷 度。粗 t，和/ 適的加 ，雖然 濟。至 鉑板材 鉑板材 接中， 該等重 以使一 -21 - 201249575 電流通過該輥，以實現加熱該鉑板材。該輥可以足夠寬， 以便貫穿該等有待連接的邊緣的整個寬度將其邊緣壓緊， 但是也可以更窄》爲了獲得一基本上與該鉑板材的厚度一 樣厚的壓焊接頭，將要求一後續步驟例如噴九加工或錘 焊。 應在上面提到的溫度下進行錘焊，並且可藉由將即將 連接的所述邊緣置於一砧上，局部加熱（例如用一氣炬） 並錘擊該等有待連接的邊緣以形成該擴散黏結，從而很容 易地進行錘焊。 噴九加工係一冷加工工藝，其中可用稱爲九的小的球 形介質蟲炸一部件的表面，該部件可包括一焊縫。例如， 該九可以是玻璃珠、陶瓷球或鋼九。由噴九加工獲得的好 處例如顯著提高疲勞壽命係殘餘壓應力和引起的冷加工的 影啓的結果。 利用玻璃珠、陶瓷球或鋼珠噴九加工該焊縫。對於該 鉑板材，玻璃珠係特別有用的。 進行該焊縫噴九加工的條件取決於噴九過程中所選的 九的品質、該九的衝擊強度以及工件的覆蓋度而有所變 化。噴九介質必須是大小均勻的，並且基本上是球形，沒 有鋒利邊緣或破碎顆粒。由一校準帶中的硬度變化確定衝 擊強度，該校準帶伴隨所希望的樣品的噴九加工。適當的 噴九加工強度的選擇取決於具體的樣本、幾何形狀和材 料。覆蓋控制係在噴九加工過程中衝擊樣本表面所能達到 的那種程度。當藉由重疊噴九凹窩而完全阻塞焊接材料的 -22- 201249575 原始表面時’獲得了完全覆蓋。典型地，該九由平均直徑 範圍從大約0_1 mm至5 mm且實質上均句、基本上爲球 形的顆粒組成。噴九可進行範圍從大約5_6〇 sec/cn^的時 間段’或者直到該校準帶顯示弧高（或彎曲）爲〇」5 mm 至〇.6 mm’並且獲得了基本上完全覆蓋。η個週期 ("C η ” ）後的覆蓋百分比等於！-(丨-c 1)，其中“ η ” 係週期數，並且“ C 1 ”係第一週期後的覆蓋百分比。通 常，獲得基本上完全覆蓋所要求的週期數在1至10的範 圍內變動。 顯然’對於該等壓焊方法，從有待連接的所述邊緣的 一側開始施加一用於焊接的力，因此必須在該鉑板材的相 反側上存在某一底座，例如一砧。除了適合各自的壓焊操 作以及機械力承受能力和與此相關的溫度之外，通常該支 架並沒有具體限制。通常，抗拉強度爲大約800 N/mm2至 大約1 100 N/mm2的鋼（例如RGM 1 7鋼）係合適的。在 輥式縫焊接的情況下，底座區（bay)係與該舶板材的該 等有待連接的邊緣的另一側上的一第一輥相反設置的一第 二輥。在本發明的另一實施方式中，該壓焊方法在一個已 預熱的底座上進行，並且其中至少一個鉑金屬板部分置於 該底座上。更確切地說，將該底座預熱到 300°C至 600°C，尤其是 3 50°C 至 550°C，或者 400°C 至 500°C。 這種預熱係有利的，以便在高溫下進行壓焊，從而避免該 底座具有一散熱器的效果。 爲了避免該鈾板材和該焊接物品翹曲，遵循一定的加 -23- 201249575 工進度（working schedule)可能是有用的。因此，在本 發明的又另一實施方式中，在所述重疊邊緣的熔體焊接部 分上從該板材的一側開始進行壓焊，並且沿著所述重疊邊 緣繼續至該板材的相反側。可替代地，從該板材兩側之間 大約中間的一距離開始進行壓焊，並且沿著所述重疊邊緣 繼續至該板材的一側，隨後從大約中間的所述距離開始至 該板材的相反側。某些情況下一些加工進度會更有用，但 是技術人員能夠藉由一些實驗發現用於各自目的的最佳進 度。 在本發明的一具體®施方式中，該等有待相互連接的 邊緣在它們的整個長度上重疊，在該鈾板材的兩側面邊界 上進行熔體焊接，建立熔體焊接連接，並且從該板材兩側 之間大約中間的一距離開始進行壓焊，並沿著所述重疊邊 緣繼續至該板材的一側，隨後從大約中間的所述距離開始 至該板材的相反側。 在本發明的又另一實施方式中，該等有待相互連接的 邊緣在它們的部分長度上進行重疊，並且在該鈾板材的一 側面邊界上熔體焊接連接。在這個實施方式中，該鉑板材 的該等邊緣通常在該鉑板材的一側面邊界上重疊，並且靠 近該側面邊界焊接連接，同時所述邊緣彼此之間距離較 大，進一步遠離各自的側面邊界。在這種情況下’兩個邊 緣通常隔開，在所述邊緣之間形成一 V形間隙’並且在 該間隙的一側面邊界上重疊並部分熔體焊接連接’同時在 相反側面邊界上不存在重疊或熔體焊接接頭’並且在所述 • 24- 201249575 重疊邊緣的熔體焊接部分上從該板材的一側開始進行壓 焊’並沿所述重疊邊緣繼續至該板材的相反側。這樣，隨 後在壓焊過程中該V形間隙將會變窄，並最終封閉該間 隙。機械加工進度的該等說明特別適於採用噴九加工和/ 或錘焊作爲壓焊方法’但是也可與其他方法一起使用。 如上所述對於其中採用1至10次的噴九加工，可以 重複各自的壓焊步驟。例如，如果有必要，也可利用錘焊 或輥式縫焊接進行相同的操作。 也可組合採用所述壓焊方法；例如，首先，一輥式縫 焊接可用於初步連接所述邊緣，然後噴丸加工該等有待連 接的邊緣，以降低厚度並實現擴散黏結，然後錘焊，以實 現表面結構的改善。另外，對於特定目的，可採用首先噴 九加工然後錘焊，或者相反。 在該壓焊步驟後，去除該焊接物品周邊上的該等熔體 焊接的部分。這可藉由切斷、使用金屬剪、切割輪、線侵 蝕、噴射切割、鐳射切割及其組合實現。或者，可使由該 去除步驟生成的邊緣平滑、硏磨所述邊緣或者以另一方式 加工所述邊緣，以去除尖銳邊緣或者獲得一所希望的表面 結構。 本發明還提供了額外的後處理步驟，可在去除所述熔 體焊接部分後或者壓焊後但是去除所述熔體焊接部分前實 施所述後處理步驟。此類後處理步驟如下所述。 在壓焊後，對由壓焊生成的縫進行冷或熱成型，以使 該縫平滑和/或減少其厚度。在這個過程中，厚度較佳的 -25- 201249575 是減少到原始金屬板厚度（to)的0.9至1.2倍，進一步 較佳的是減少到大約原始金屬板厚度（to)。然後，也可 藉由磨損和拋光該縫而對該縫（如果適當的話，連同整個 表面）進行一表面拋光，以獲得一均勻的表面品質。 在一額外任選的後處理步驟中，壓焊後在大約900°C 至大約1400°C，較佳的是大約1000°C至大約 溫度下進行熱處理（“去應力退火”）。 此外，根據本發明，較佳的是，所述重疊安排涉及將 所述金屬板部分中的一直接置於另一上方/下方。因此， 在所述金屬板部分之間沒有焊接塡料和/或箔。根據本發 明，例如如DE 1 527299的圖1所示，也沒有使用繃帶， 這意味著沒有額外的管段或金屬板置於該等將被引入到有 待連接的邊緣之間的擴散黏結中的金屬板的重疊部分的上 方或下方。已經發現，然而，本發明獲得了比習知技術更 好的蠕變斷裂強度。 已經發現，經過上述焊接技術處理的彌散強化鉑基合 金在大體上相當於該基礎金屬的焊接物品中產生了微觀結 構，並且獲得了相當於該基礎鉑板材的優異的機械特性。 較佳的是，以這樣一方式控制該方法，使得該冷或熱成型 後’該縫的寬度爲原始金屬板厚度（tO)的大約5至大約 1〇倍，並且進一步較佳的是爲原始金屬板厚度（t0)的大 約6至大約7倍。根據本發明，在一冶金顯微磨片中，不 能確定由根據本發明的方法獲得的該縫與沒有縫的鄰近金 屬板部分之間的區別。因此，本發明還涉及一種可由本發 -26- 201249575 明的方法獲得的彌散強化鉑基合金板材的焊接物品。 本發明在此進一步進行說明，但是不限於以下給出的 實例。在所有實例中，該等測試樣品由包含鉑的彌散強化 合金製造，並且由快速固化的粉末藉由上述壓緊和製造技 術製備。列舉的說明本發明原理的具體技術、條件、材 料、比例和報告數據係示例性的，並且不應理解爲限制本 發明的範圍。出於所有有用的目的，在此引用的文獻藉由 引用結合到本申請中，並且因此屬於並補充本發明的揭露 內容。 附圖詳細說明 圖1中，可看到兩個金屬板部分，一第一金屬板部分 1以及一第二金屬板部分4，並且在該實施方式中，該等 金屬板部分具有相同或者至少非常相似的金屬板厚度to。 該等厚度可以彼此不同。以一直線方式向外（即在背向各 自鄰近金屬板部分的那側上）將所述金屬板部分的兩端進 行倒角，因此以一倒角角度形成倒角3和6，倒角寬度用 F表示。根據本發明的一方面，因此，以這樣一方式定向 該等倒角，使得在所述金屬板部分不連接的狀態下，這兩 個金屬板部分不在一平面上或者基本上不在一平面上。在 一重疊寬度爲ϋ的重疊區域中，將隨後有待與這兩個金 屬板部分接觸的各自接觸部分2和5彼此相反設置，有可 能粗化該等接觸部分。該重疊寬度ϋ總是大於該對角寬 度F。 -27- 201249575 在該圖中，該第二金屬板部分4置於一個已經預熱或 者仍要加熱的底座1 0如一砧上。在這種情況下，應將熱 量最初從所述底座轉移到所述第二金屬板部分4，並且， 如果合適的話’還轉移到所述第一金屬板部分1。如果所 述第一金屬板部分1的一部分也置於所述底座10上，也 可直接轉移熱量。可用一具有一夾緊力FE的調准裝置 (未示出）夾緊金屬板部分1和4。總體上，所述調准裝 置藉由所述夾緊的金屬板部分僅與所述底座1 〇間接相 連。該等調准裝置的目的僅僅是保持所述金屬部分連接到 所述底座10，但是不保持金屬板部分1和4在一起，因 爲這藉由熔體焊接連接實現。 圖2a和2b顯示了一實施方式，其中一金屬板1彎 曲’以形成一管狀物品。所述倒角邊緣設置在彼此之上 2 ’並且在該金屬板3的周邊上，該等邊緣與—或兩個熔 體焊接接頭4相互連接。在圖2a中，該金屬板3的周邊 和該熔體焊接接頭4位於一端耳5上，該端耳僅用於此目 的’當熔體焊接後切掉該端耳5時，該端耳用於使金屬損 耗減到最少。注意在2a和2b兩者中，所述熔體焊接接頭 靠近該鉑板材的側面邊界。 【圖式簡單說明】 當參考本發明的較佳實施方式的以下詳細說明和附圖 時’本發明將得到更充分地理解，並且進一步的優點將變 得明顯，在該等附圖中： -28- 201249575 圖1示出了置於一支架上具有倒角的邊緣的板材； 圖2a和2b示出了 一熔體焊接步驟後被安排爲一管狀 物品的板材。201249575 VI. Description of the Invention [Technical Field of the Invention] FIELD OF THE INVENTION The present invention relates to dispersion strengthened platinum-based alloys and, more particularly, to a method for welding such alloys. [Prior Art] 2. Description of the Prior Art Structural parts composed of precious metals and precious metal alloys such as preferably PGM materials are used in the glass industry, particularly in specialty glass melting and thermoforming plants. These plant components for fusion technology, also known as PGM (Platinum Metal) products, are used to melt, refine, transport, homogenize and dispense the liquid glass. Most of these precious metal alloys are platinum-based alloys in which cerium, lanthanum or gold is added to the alloy. Oxide dispersion strengthened uranium-based alloys are increasingly used if very high structural part strengths are required due to mechanical and/or thermal stresses imposed by the glass melt, since such platinum-based alloys are characterized by a specific alloy Higher ability to withstand thermal, mechanical and chemical stresses. An oxide dispersion alloy (hereinafter also referred to as an ODS alloy) differs in a very uniform microstructure. Factory parts with glass melts are often precious metal sheet structures designed as thin-walled piping systems. The molten glass flows through the parts at a temperature between 1 000 ° C and 1700 ° C. Due to the high melting point of PGM (platinum group metal) materials, they differ in their high temperature resistance and, in addition, in high mechanical strength and wear resistance, and are therefore particularly suitable for structural parts in production equipment or Equipment parts in contact with the glass melt. Suitable materials are uranium and alloys of platinum and/or other PGM metals, which may also optionally contain minor amounts of basic metals as additional alloying components or oxidizing additives. Typical materials are refined lead, platinum-rhodium alloys and platinum-rhodium alloys, which contain small amounts of finely divided fire-resistant metal oxides such as, in particular, zirconia or yttria to improve strength and high temperature creep resistance. However, in addition to selecting the suitable material, the production of such precious metal parts, particularly forming, also plays an important role in determining strength. Typically, the components from separate metal sheets are joined together to provide the desired geometry and are typically interconnected by melt welding. In this process, the metal sheets to be interconnected by heat supply are used. The joint between the two is converted into a molten state, and, where appropriate, a same type of entangled material is converted into a molten state and fused together. In this case, the heat of fusion can be generated by an electric arc or an ignition gas-oxygen mixture. However, if components joined in this manner are exposed to very high temperatures, such as above 1 200 ° C, the weld often forms a weak point in the bond of the overall material. The reason that has been determined is the unevenness in the weld and the change in the microstructure in the heat affected zone. In particular, longitudinal structural welds in cylindrical structural parts such as pipes have a specific risk due to the applied stress, which is almost twice as high as that of the circumferential weld, and therefore these longitudinal welds are often unacceptable and cracked. When using known welding processes such as tungsten inert gas (TIG) welding, plasma welding, laser or self-welding, the alloy is melted "« but during use above 1 200 ° C, due to recrystallization When melting the classic 201249575 replacement solid solution alloy, only a small loss of strength can be observed in the weld, and the melting of the weld oxide dispersion strengthened alloy results in Zr02 and/or Υ2〇3 in the melt. Most of the dispersions condense and float. A coarse granulated solidified microstructure is formed in the weld. Therefore, the strengthening effect of the dispersion in the weld is invalid. Then the stress withstand capability of a component joined together in this manner and its service life are reduced to the level of the connected component from the standard alloy. Measures for preventing such a disadvantage are known from JP 5 2 1 2 5 77 Α and ΕΡ 03 20877 B1. In the method disclosed herein, a fused weld on the ODS metal plate is then covered with a Pt-ODS foil and pressed into the seam by hammering at elevated temperatures. This measure increases the fineness of the particle size distribution of the weld by the foil and thereby reduces the likelihood of crack formation on the surface. In addition to the additional outdated alternatives, the integral joints formed by hammering the welds have been resorted to. However, the quality of this type of joint is greatly variable. In order to eliminate these changes, great expense is required to prepare the weld and to require very precise control of the process parameters during the welding process. In the case of this process, it has proven to be very difficult to uniformly heat the two materials to be joined during hammering, especially metal sheets. In doing so, it is almost impossible to fully heat the lower metal plate with the torch at the welding position to achieve a good bonding effect during the hammering process. The process is therefore very difficult 'does not necessarily lead to an optimal result and is very expensive. In addition, there is a fundamental problem in the manufacture of hammered welds, because in the case of alloys with a niobium content of more than 4% by weight and usually in the case of 0DS alloys, the material has a low tendency to stick during hammering. . It has been deposited 201249575 that the oxides in the ODS material and/or the oxides formed during the hammering process, mainly yttrium oxide, significantly reduce the bonding of the two structural parts, particularly the metal sheets. The poor adhesion has the effect of significantly increasing production expenditure, but at the same time has the effect of increasing the risk of not getting sufficient adhesion in certain areas of the joint region in the seam. In DE 1 023 7763 B4, in the production of permanent integral joints of structural parts of oxide-dispersed (ODS) metal materials, the welding of the individual materials takes place separately below their melting temperature, wherein at least partial formation takes place in the connection region. A diffusion bond. In a second process step, the diffusion bonding, preferably the entire joint region, is heated to a temperature which is also lower than the melting temperature of the material and/or structural component to be interconnected, and mechanically at this temperature Re-compacting, preferably hammering. The two materials to be interconnected in this case define the connections before the welding operation, the latter usually forming the joining region, ie the two materials desired to be produced are to be produced. The area of the joint between. In this process, a permanent integral joint of oxide-dispersed (ODS) metal structural parts is provided by arranging for diffusion bonding bonding for production prior to mechanical re-compaction under heating. A preferred embodiment provides the use of a solder paste. The solder paste is arranged in a joint region between the two materials and/or structural parts of the oxide-dispersed metal material to be connected to each other. Here, the solder paste may be a separate component or a coating of at least one of the connecting faces opposite each other in the connecting region. Specifically, a suitable welding material in this case is a ductile fusion alloy such as PtAu5, Ptlrl, pure Pt, but also a more robust alloy, such as PtRh5, PtRhlO, Ptlr3. The document emphasizes that due to the substantial increase in the tendency to bond between the two materials, the solder paste can achieve a significantly improved bond between the two materials to be interconnected, and this in turn greatly reduces production costs. In addition, the ability of the joint region to withstand thermal and mechanical stresses should be significantly improved. In addition, the document emphasizes the particularly good insertion of a precious metal foil. In a preferred embodiment, the document teaches that the edges of the metal sheets to be joined are chamfered and placed above each other, wherein the edges of the chamfers are precisely above each other, and In a freezing step, a diffusion bond is first temporarily attached, and the diffusion bond is mechanically re-compacted to achieve final diffusion bonding in a subsequent step. A disadvantage is that the chamfered portions of the edges face each other and overlap exactly 'in particular, when a mechanical load is applied, this will result in a thinner diffusion bond or a lower strength diffusion bond than the other metal plate, both Both result in a lower strength of the bond. Furthermore, it is disadvantageous to use a solder paste or foil of a different composition than the metal plate to be joined, since the resulting Kirkendall-Effect will result in the formation of pores, thereby weakening the edges. Welded joint between. SUMMARY OF THE INVENTION The present invention is based on the object of providing a device for attaching an oxide-dispersed precious metal plate, an improved method, and a device for carrying out the method. BRIEF SUMMARY OF THE INVENTION -9 - 201249575 The present invention relates to a method of preparing a welded article in accordance with the following: 1. A method for producing a welded article of a dispersion strengthened platinum-based alloy sheet comprising the steps of providing at least one dispersion strengthened platinum-based alloy a sheet; chamfering an edge of the dispersion-strengthened uranium-based alloy sheet to be welded: overlapping the edges of the chamfers to be welded; the overlapping chamfered edges of the dispersion-strengthened platinum-based alloy Melt welding is performed only on the periphery of the edge; the platinum plate is welded by a pressure welding method to produce the weld, and the pressure welding method is selected from the group consisting of hammer welding, spray machining, roll seam welding, and resistance welding. , diffusion welding, friction welding, and combinations thereof; removing the melt-welded portion on the periphery of the welded article. The method of item 1, wherein the melt-welding step is TIG welding (tungsten inert gas welding), The TIG welding includes the following steps: a. adjusting the TIG welding power source to minimize energy input into the weld; b. Contacting the arc gas composition to maximize quenching of the weld; c. contacting the weld with a second gas, the contact being primarily at the bottom surface of the weld to quench the underside of the weld d. contacting the weld with a trailing gas to enhance cooling of the weld beyond the cooling achieved by the arc gas and the second gas. 3. The method of item 1 or 2, wherein the welded article is a tubular article, and the edges to be joined belong to the same platinum-based alloy material -10- 201249575 plate. 4. The method according to any one of items 1 to 3, wherein the platinum-based alloy has a component consisting essentially of gold, ruthenium or osmium, in particular selected from the group consisting of PtAu5, Ptlr 1, PtRh5 , PtRhl 0, PtRh20, Ptlr3, Ptlr5 pure uranium and alloy composition of the combination. 5. The method of any of clauses 1 to 4, wherein the uranium-based alloy is oxide-dispersion strengthened with an oxide derived from cerium oxide, zirconium dioxide, and mixtures thereof. group. 6. The method according to any one of items 1 to 5, wherein the platinum-based alloy has a composition of PtAu5, Ptlrl, PtRh5, PtRhlO, Ptlr5 or Ptlr3, and is oxide-dispersed with cerium oxide or zirconium dioxide. . 7. The method of any of clauses 1 to 6, wherein the removal of the melt welded portions is accomplished by cutting, metal shearing, cutting wheels, wire erosion, jet cutting, laser cutting, and combinations thereof. 8. The method of any of items 1 to 7, wherein the melt welding method is selected from the group consisting of: plasma welding, laser welding, TIG (tungsten inert gas) welding , resistance welding or self-welding welding. 9. The method of clauses 2 to 8, wherein the power supply is a pulse inverter. 10. The method of clauses 2 to 9, wherein the arc gas has a composition selected from the group consisting of: gas, ammonia, and mixtures thereof. The method of any one of items 2 to 10, wherein the -11 - 201249575 two gas system is a gas mixture. The method of any one of clauses 2 to 11, wherein the tail gas is selected from the group consisting of: gas, nitrogen, helium, carbon dioxide, and mixtures thereof. 13. The method of clause 2, wherein the second gas is selected from the group consisting of argon, nitrogen, helium, carbon dioxide, and mixtures thereof. 14. The method of item 2 wherein the contact is held by a cooled clamp. 15. The method of item 2 wherein the tail gas is applied by a gas nozzle and the nozzle quenches the weldment by conduction. 16. The method of clause 1, wherein the jetting processing medium is selected from the group consisting of glass beads, ceramic balls or steel nine. The method of item 1, wherein the jetting processing step is performed for a period of time ranging from about 5 sec/cm 2 to 60 sec/cm 2 . 18. The method of clause 1, wherein the nine are comprised of substantially uniform, substantially spherical particles having an average diameter ranging from about 0.1 mm to about 5 mm. 19. The method of clause 1, wherein the melt welding is performed on the edge of the edge only on one side of the sheet. 20. The method of clause 1, wherein the melt welding is performed on the edge of the edge only on one side of the sheet, and the edges of the chamfer are not heavy on the opposite side and are arranged separately from each other. The method of item 1, wherein the at least two metal plate portions -12-201249575 are arranged to overlap, and the chamfered edges extend outwardly to the plate portion. The method of item 1, wherein the welded base is performed by a pressure welding method, and three of the parts are placed on the base. 23. The method of item 22, wherein 300 ° C to 600 ° C, preferably 350 ° C to 550. It is 400 ° C to 500. The method of item 1, wherein the echo width (F) is 1 to 2 times the original metal plate width (t0) and/or the chamfer angle is 15. To 27c 17 The method of item 1, wherein the melt-welded portion of the pressure-welded house is from the sheet of the sheet, further preferably from about 19.6. The side begins to enter the edge of the f and continues to the opposite side of the sheet. 26. The method of item 1, wherein the pressure welding name is performed at approximately the middle point, and along the side of the sheet, From the opposite side of the said point about the middle. 27. A welded article of a dispersion-strengthened platinum-based alloy sheet is obtained by the method of item 1. [Embodiment], the distance from the adjacent gold I is connected One preheated g less than one metal plate, the base is preheated to C, further preferably with a chamfer of 3 times the edge, preferably ', preferably from 23.6°, and the most E such overlapping edges ί, And continuing along the edge of the crucible on both sides of the sheet to the crucible article of the sheet, the weld-13-201249575 DETAILED DESCRIPTION The present invention provides a method for welding a dispersion strengthened platinum-based alloy. The melt welding convention of the present invention is such that when compared to the base metal, the rough brittle metal of the prior art method is significantly reduced or eliminated. The formation of inter-compound features, and the formation of such features severely reduces the joint strength and ductility of the welded article. The weld can be machined to homogenize the weldment and heat affected zone. According to the present invention, A cost effective way to weld a dispersion strengthened uranium-based alloy and thus retain its useful mechanical properties. In one aspect of the invention, a weld is produced from a dispersion strengthened platinum-based alloy sheet. Specifically, the alloy is welded by a method The method comprises the steps of: providing at least one dispersion-strengthened platinum-based alloy sheet; chamfering an edge of the dispersion-strengthened platinum-based alloy sheet to be welded; and overlapping the edges of the chamfers to be welded The edges of the overlapping chamfers of the dispersion strengthened uranium-based alloy are only performed at the periphery of the edge Body welding; the platinum sheet is welded and joined by a pressure welding method to produce the weld seam, the pressure welding method is selected from the group consisting of: hammer welding, spray nine processing, roll seam welding, electric resistance welding, diffusion welding, friction welding And a combination thereof; the melt-welded portion on the periphery of the welded article is removed. For example, as described in EP 0320877, US-B-6511523 or EP 1781830, a suitable dispersion-strengthened platinum-based alloy sheet can be provided. In the present invention - In one embodiment of 14-201249575, the uranium-based alloy forming the platinum sheet has a component mainly composed of platinum together with gold, ruthenium or osmium, especially selected from the group consisting of PtAu5, Ptlrl, PtRh5, PtRhlO, PtRh20 An alloy of the group consisting of Ptlr3, Ptlr5, pure platinum, and combinations thereof. In another embodiment, more specifically, the platinum-based alloy may be subjected to oxide dispersion strengthening using an oxide selected from the group consisting of cerium oxide, a oxidized pin, and a mixture thereof. In this regard, the patent documents cited above describe this. This oxide dispersion strengthening may be present in pure platinum and in the alloys disclosed above in this section, depending on the desired material properties. More specifically, the uranium-based alloy has a composition of PtAu5, Ptlrl, PtRh5, PtRhlO, Ptlr3, Ptlr5 or pure platinum, and oxide dispersion is carried out using cerium oxide or chromium dioxide. According to another aspect of the invention, it is preferred to chamfer the edge, in particular in a straight line. Here, when the metal plate portions are arranged to overlap, the metal plate portions to be joined are connected in such a manner that the chamfered edges then extend outward, i.e., away from the adjacent metal plate portions. It has been found that chamfering and aligning portions of the sheet metal in this manner increases the creep rupture strength of the joined product. This is shown in more detail below. Also in this case, the metal plate portion is subjected to diffusion hammer welding. A preferred method in accordance with the present invention also includes the two aspects discussed above, namely providing and preheating a base and forming the chamfer in a proposed manner. The chamfered width (F) of the chamfered edge is preferably from 1 to 3 times, preferably 2 times, the original metal plate thickness (t0). Further preferably, the chamfer angle α is from about 15° to about 27. Preferably, -15 to 201249575 is from about 17.6° to about 25.6°, further preferably from about 19.6° to about 23.6°, and most preferably about 21.6°. Preferably, the chamfered edges are shaped such that the chamfered portions of the edges are parallel or at least substantially parallel to one another, which means that when the chamfered portions are arranged to face each other When the two edges complement each other. This is often the case when the chamfer angles α of the two edges are the same. These edges are then overlapped. In another embodiment of the present invention, as depicted in FIG. 1 and described below, the edge overlap is performed in such a manner that when the metal plate portions are arranged to overlap, the chamfered edges It then extends outwardly, ie away from the adjacent sheet metal portion. In still another embodiment of the present invention, the edges to be joined belong to the same plate of platinum-based alloy material, so the plate of molybdenum material has to be bent to allow the edges to be re-exposed so that the welded article will be a tubular object. The cross section of the tubular welded article is not particularly limited and may be, for example, a circle, an ellipse or a polygon. Preferably, the metal plate portions are arranged to overlap, wherein the overlap length is 2.5 to 7.5 times the original metal plate thickness (to), preferably 4 to 7 times the original metal plate thickness (t0). After the diffusion welding, the overlap of the metal plate portions is 3 to 8 times the thickness (t0) of the original metal plate, preferably 5 to 7 times the thickness (t0) of the original metal plate. The overlapping edges are then melt welded at the periphery of the edges. During the melt welding process, the dispersion can condense, so the strengthening of the dispersion in the weld will be ineffective or at least limited. Since the melt-welded parts are cut off later in the process, the properties of the final product -16-201249575 will not be affected. In principle, as long as the energy input into the platinum sheet is not limited 'the method for melt welding is not limited to a specific method' such that the melting and solidification of the dispersion is not limited in space to the melt-welded joint. Area. The melt welding method can be generally selected from the group consisting of plasma welding, laser welding, TIG (tungsten inert gas) welding, electric resistance welding or self-welding welding. The skilled person is familiar with these common melt welding methods and knows how to achieve the objects of the present invention using such melt welding methods. Melt welding on the periphery of the edge may be performed only on one side of the platinum sheet or on both sides of the uranium sheet. It is apparent that the weld heads are placed on the overlapping edges such that the overlapping edges are welded at this particular location. Generally, the melt welded joint does not need to have a large size, and a single weld is sufficient. As depicted in Figures 2a and 2b, the weld head will be placed around the edge of the edge to be joined, near the side boundary of the uranium sheet. In still another embodiment of the invention, the edges to be joined to each other overlap over their entire length, and melt welding is performed on both side boundaries of the platinum sheet, and a melt welded joint is established. In still another embodiment of the invention, the melt welding is performed on only one side of the sheet material on the periphery of the edges, and the diagonal edges do not overlap on the opposite side and are arranged to be separated from each other. In this embodiment, the edges to be joined to each other overlap over a portion of their length and are melt welded at one of the side boundaries of the plate. In this embodiment, the edge -17-201249575 of the slab is generally overlapped on a side boundary of the uranium sheet and weldedly joined adjacent to the side boundary, while the edges are separated from each other The side boundaries are far apart. In this case, the two edges are usually spaced apart to form a V-shaped gap between the edges and overlap and partially melt-weld at one of the side boundary ends of the gap, while on the opposite side boundary There are no overlapping or melt welded joints. In still another embodiment of the present invention, the edges to be joined to each other overlap over their partial lengths or their entire length, and the periphery of the platinum sheet on which the fusion welded joint is to be placed On a section, the section extends beyond the lateral boundaries of the remaining platinum sheets. In other words, the platinum sheet on the edges to be joined is wider than the expected width of the remainder of the welded article to form a terminal ear and the end ears are cut after the pressure welding step is performed, the end ears It is only possible to save the purpose of providing a solder joint which is spatially separated from the portion of the edge to be joined. In this way, the amount of uranium sheet being cut and recovered can be minimized and the working time and effort used for this step are minimized. Such a situation is depicted in Figure 2a. In another embodiment of the invention, TIG (Tungsten Inert Gas) welding is a suitable method for the purposes of the present invention. More specifically, the TIG welding includes the following steps: a. adjusting the TIG welding power source to minimize energy input into the weld; b. contacting the weld with an arc gas composition, the combination The material is adjusted to maximize quenching of the weld; -18- 201249575 C. The weld is contacted with a second gas, the contact being primarily at the bottom surface of the weld to quench the underside of the weld And d. contacting the weld to a tail gas to enhance cooling of the weld 'to exceed the cooling achieved by the arc gas and the second gas" to input energy into the weld Examples of minimized TI G welding power sources include, but are not limited to, those utilizing inverter technology that produces pulsed alternating current (AC) waveforms that increase response speed. The pulsed inverter power supply produces a highly stable arc with a minimum current that is maintained by a square wave AC pulse that is completely different from conventional alternating current. This type of arc is advantageous for welding thin platinum sheets, the process of which is often difficult and allows for high speed welding. The pulse inverter also produces a more concentrated arc that allows for more accurate energy input into the weld. This feature is the key to controlling the rapid solidification properties of the weld. This is achieved because the high-speed pulse from 10 Hz to 500 Hz concentrates the arc at a very fine point, while the stability of the arc is improved. . Finally, the high pulse rate enhances electrode cleaning, allowing the weld to be reversed or the cleaning cycle reduced. This again reduces the amount of energy input into the system. Not only controlling the arc gas mixture or various gas mixtures in the welding arc but also controlling the bottom side of the weld and directly controlling the weld itself improves the cooling rate of the weld and is thus available in the weld A fast solidified structure is obtained. The type of clamp and gas nozzle used to protect the front and back of the weld is different and depends on the configuration of the 19-201249575 component to be welded and the type of joint to be formed. The arc gas composition is argon or nitrogen or a mixture of the two. The covering gas (tail gas) for protecting and quenching the bottom side of the weld is argon, nitrogen, ammonia or carbon dioxide or a combination of two or more of these gases. In order to increase the quenching speed of the jig, the jig itself can be cooled. The cover gas system applied through the tail gas nozzle is argon, nitrogen, helium or carbon dioxide or some combination of two or more of these gases. The gas nozzle is in physical contact with the welded article to quench the welded article by conduction. TIG welding is satisfactory according to the industry because it is easy to apply and widely deployed. Therefore, by utilizing a TIG power supply that minimizes the energy required for soldering, an optimum combination of the shielding gas for cooling the weld as quickly as possible is employed, and the joint is appropriately tightened to mainize a quenching gas. For the TIG welding, the bottom side of the weld is immediately tailed at the point of the weld. Preferably, due to its ability to form an agglomerated arc at high pulse rates, a pulsed AC inverter power supply is utilized to reduce the energy required for soldering. Preferably, the arc and shielding gas are selected from helium, argon or a mixture thereof that provides the desired maximum quenching rate. Fixtures and horseshoe nozzles are used to optimize weld ease of use, and their placement and design will vary depending on weld configuration and part geometry. Typical quenching and shielding gases are selected from the group consisting of argon, helium, nitrogen, carbon dioxide, and mixtures thereof. Subsequently, the platinum plate is welded and joined by a pressure welding method to form the weld -20-201249575 seam, and the pressure welding method is selected from the group consisting of hammer welding, spray machining, roll bonding, electric resistance welding, diffusion welding, friction welding, and the like. Its combination. These welding methods are below the melting temperature of the platinum sheet and are familiar to those skilled in the art who will find the best results after several experiments. However, it is preferred to carry out the methods at temperatures above room temperature but at the temperature of the melting. It can be at a temperature of from about 1 000 ° C to about 1, more specifically about 1,200. (: to about 1 300 ° C, about 1400 ° C to about 1 600. It is preferable to carry out such a pressure welding at a temperature of <:, wherein the metal plate portion is arranged to overlap the metal plate portions to be roughened on the mutually facing sides, preferably, the degree Ra is From about 0.05 μm to about 25 μm, further preferably from about 0.5 μm to about 10 μm. It may have been cut off with a defined cutting edge during the chamfering process or by subsequent surface processing such as honing with undefined cutting edges, thereby providing such roughening which makes it possible to provide an increase in the diffusion welded area. The surface seek or make it possible to increase the controllability of the welding parameters as much as possible. For example, the heating method is a gas torch. It is possible to locally heat the portions of the metal sheets to heat the entire range to be pressure welded, but often without friction welding, particularly friction stir welding, a suitable method for joining them. Resistance welding provides for the heating of the edges to be joined by passing an electric current through the edge to be joined. In roll seam welding, a roll is pressed along the edges to be joined to press the edges of the stack of platinum sheets and thereby form a diffusion bond. At the same time, the cold seam of the seam welder can be 1 700 °C or larger. Into the rough, the surface is cut by the edge. Thick t, and / appropriate plus, although the economy. To the platinum plate platinum plate, the weight is such that a current of -21 - 201249575 is passed through the roll to heat the platinum plate. The roller may be wide enough to press its edges through the entire width of the edges to be joined, but may also be narrower. In order to obtain a pressure welded joint substantially as thick as the thickness of the platinum sheet, a requirement of one will be required. Subsequent steps such as jetting or hammering. Hammer welding should be carried out at the temperatures mentioned above, and the diffusion can be formed by placing the edges to be joined on an anvil, locally heating (for example with a torch) and hammering the edges to be joined to form the diffusion. Bonding makes it easy to hammer weld. The blasting process is a cold working process in which a small spherical medium called ninth is used to blow the surface of a part, which may include a weld bead. For example, the nine may be glass beads, ceramic balls or steel nine. The advantages obtained by the jetting process, for example, significantly increase the residual compressive stress of the fatigue life and the resulting cold work. The weld is machined by glass beads, ceramic balls or steel balls. Glass beading is particularly useful for this platinum sheet. The conditions for performing the weld bead processing vary depending on the quality of the nine selected during the ninth process, the impact strength of the ninth, and the coverage of the workpiece. The spray medium must be uniform in size and substantially spherical with no sharp edges or broken particles. The impact strength is determined by the change in hardness in a calibration strip that is accompanied by the desired nine-pass processing of the sample. The choice of the appropriate spray strength depends on the specific sample, geometry and material. The coverage control is the extent that can be achieved by impacting the surface of the sample during the jetting process. Full coverage was obtained when the -22-201249575 original surface of the solder material was completely blocked by overlapping the nine dimples. Typically, the nine are composed of substantially uniform, substantially spherical particles having an average diameter ranging from about 0 to about 1 mm to about 5 mm. The jetting can be performed for a period of time ranging from about 5-6 sec/cn^ or until the calibration strip shows an arc height (or bend) of 〇"5 mm to 〇.6 mm" and substantially complete coverage is obtained. The coverage percentage after η cycles ("C η ”) is equal to !-(丨-c 1), where “η ” is the number of cycles, and “ C 1 ” is the percentage of coverage after the first cycle. The number of cycles required for complete coverage varies from 1 to 10. It is clear that for these pressure bonding methods, a force for welding is applied from the side of the edge to be joined, so the platinum must be There is a certain base on the opposite side of the sheet, such as an anvil. In addition to being suitable for the respective pressure welding operation as well as the mechanical force bearing capacity and the temperature associated therewith, the bracket is generally not specifically limited. Usually, the tensile strength is about Steels from 800 N/mm2 to about 1 100 N/mm2 (for example RGM 17 steel) are suitable. In the case of roll seam welding, the base area is the edge to be joined to the plate. A second roller disposed opposite to a first roller on the other side. In another embodiment of the invention, the pressure bonding method is performed on a preheated base, and wherein at least one portion of the platinum metal plate Placed on the base. Specifically, the base is preheated to 300 ° C to 600 ° C, especially 3 50 ° C to 550 ° C, or 400 ° C to 500 ° C. This preheating is advantageous, so that at high temperatures Pressure welding is performed to avoid the effect of the base having a heat sink. In order to avoid warping of the uranium sheet and the welded article, it may be useful to follow a certain working schedule of -23-201249575. Therefore, in this In still another embodiment of the invention, pressure welding is performed from one side of the sheet on the melt welded portion of the overlapping edge and continues along the overlapping edge to the opposite side of the sheet. Alternatively, Pressure welding is initiated from a distance approximately between the two sides of the sheet and continues along the overlapping edge to one side of the sheet, and then from about the middle of the distance to the opposite side of the sheet. Some processing progress may be more useful in the case, but the skilled person will be able to find the best progress for their respective purposes by some experiments. In a particular embodiment of the invention, the edges to be interconnected are in it Over the entire length of the uranium sheet, melt welding is performed on both side edges of the uranium sheet to establish a melt welded joint, and pressure welding is started from a distance between the two sides of the sheet, and along the The overlapping edges continue to one side of the sheet and then from about the middle of the distance to the opposite side of the sheet. In yet another embodiment of the invention, the edges to be joined to each other are on their partial lengths Overlap and fusion-welding joints on one side boundary of the uranium sheet. In this embodiment, the edges of the platinum sheet generally overlap on a side boundary of the platinum sheet and are welded adjacent to the side border At the same time, the edges are at a greater distance from each other, further away from the respective side boundaries. In this case the 'two edges are usually spaced apart, forming a V-shaped gap between the edges and overlapping and partially melt-welding the joint on one side of the gap' while not present on the opposite side boundary Overlap or melt-weld joints' and press-weld from one side of the sheet on the melt-welded portion of the overlapping edge of the 24-24,495,755 and continue along the overlapping edge to the opposite side of the sheet. Thus, the V-shaped gap will then narrow during the pressure welding process and eventually close the gap. These descriptions of the progress of the machining are particularly suitable for the use of the jetting process and/or the hammering as the pressure welding method' but can also be used with other methods. The respective pressure welding steps can be repeated for the jetting process in which 1 to 10 times are employed as described above. For example, the same operation can be performed by hammer welding or roll seam welding if necessary. The pressure welding method may also be used in combination; for example, first, a roll seam welding may be used to initially join the edges, and then blasting the edges to be joined to reduce the thickness and achieve diffusion bonding, and then hammer welding, To achieve an improvement in surface structure. Alternatively, for a specific purpose, it is possible to first spray and then hammer weld, or vice versa. After the pressure welding step, the melt welded portions on the periphery of the welded article are removed. This can be accomplished by cutting, using metal shears, cutting wheels, wire erosion, jet cutting, laser cutting, and combinations thereof. Alternatively, the edges created by the removal step can be smoothed, honed or otherwise machined to remove sharp edges or obtain a desired surface texture. The present invention also provides an additional post-treatment step that can be performed after removing the weld portion of the melt or after pressure welding but before removing the portion of the melt weld. Such post-processing steps are as follows. After the pressure welding, the seam formed by the pressure welding is cold or thermoformed to smooth and/or reduce the thickness of the slit. In this process, the thickness of -25 to 201249575 is reduced to 0.9 to 1.2 times the original metal plate thickness (to), and further preferably to about the original metal plate thickness (to). The seam (and, if appropriate, the entire surface) can then be surface polished by abrading and polishing the seam to achieve a uniform surface quality. In an additional optional post-treatment step, heat treatment ("stress relief annealing") is carried out after the pressure welding at a temperature of from about 900 ° C to about 1400 ° C, preferably from about 1000 ° C to about. Further, according to the present invention, preferably, the overlapping arrangement involves placing one of the metal plate portions directly above the other/below. Therefore, there is no solder paste and/or foil between the metal plate portions. According to the invention, for example, as shown in Fig. 1 of DE 1 527 299, no bandage is used, which means that no additional pipe sections or metal plates are placed in the metal which will be introduced into the diffusion bond between the edges to be joined. Above or below the overlap of the board. It has been found, however, that the present invention achieves better creep rupture strength than conventional techniques. It has been found that the dispersion-strengthened platinum-based alloy treated by the above-described welding technique produces a microscopic structure in a welded article substantially equivalent to the base metal, and excellent mechanical properties equivalent to the basic platinum plate material are obtained. Preferably, the method is controlled in such a manner that the width of the slit after the cold or hot forming is about 5 to about 1 inch of the thickness (tO) of the original metal sheet, and further preferably is original. The thickness of the metal plate (t0) is about 6 to about 7 times. According to the present invention, in a metallurgical microgrinding sheet, the difference between the slit obtained by the method according to the present invention and the portion of the adjacent metal sheet having no slit can not be determined. Accordingly, the present invention is also directed to a welded article of a dispersion-strengthened platinum-based alloy sheet obtainable by the method of the invention of -26-2012495. The invention is further illustrated herein, but is not limited to the examples given below. In all cases, the test samples were made from a dispersion strengthened alloy containing platinum and were prepared from the fast curing powder by the above-described compression and manufacturing techniques. The specific techniques, conditions, materials, ratios, and report data that are illustrative of the principles of the invention are illustrative and are not intended to limit the scope of the invention. For all useful purposes, the documents cited herein are hereby incorporated by reference in their entirety in their entirety in their entirety in the the the the the the the the the DETAILED DESCRIPTION OF THE DRAWINGS In Figure 1, two metal plate portions, a first metal plate portion 1 and a second metal plate portion 4 are visible, and in this embodiment, the metal plate portions have the same or at least very Similar sheet metal thickness to. The thicknesses can be different from each other. The two ends of the metal plate portion are chamfered outward in a straight line manner (i.e., on the side facing away from the portion adjacent to the metal plate portion), thereby forming chamfers 3 and 6 at a chamfer angle, and the chamfer width is used F said. According to an aspect of the invention, therefore, the chamfers are oriented in such a manner that the two metal plate portions are not in a plane or substantially not in a plane in a state where the metal plate portions are not connected. In an overlapping area of overlap width ϋ, the respective contact portions 2 and 5 to be subsequently brought into contact with the two metal plate portions are disposed opposite to each other, and it is possible to roughen the contact portions. This overlap width ϋ is always greater than the diagonal width F. -27- 201249575 In this figure, the second metal plate portion 4 is placed on a base 10 such as an anvil which has been preheated or still to be heated. In this case, heat should be initially transferred from the base to the second metal plate portion 4 and, if appropriate, also transferred to the first metal plate portion 1. If a part of the first metal plate portion 1 is also placed on the base 10, heat can be directly transferred. The metal plate portions 1 and 4 can be clamped by an alignment device (not shown) having a clamping force FE. In general, the alignment device is indirectly coupled only to the base 1 by the clamped sheet metal portion. The purpose of the alignment means is simply to keep the metal portion attached to the base 10, but not to keep the metal plate portions 1 and 4 together, as this is achieved by a melt welded joint. Figures 2a and 2b show an embodiment in which a metal sheet 1 is bent to form a tubular article. The chamfered edges are disposed on top of each other 2' and on the periphery of the metal sheet 3, the edges are interconnected with - or two of the weld joints 4. In Fig. 2a, the periphery of the metal plate 3 and the melt-welded joint 4 are located on one end of the ear 5, which is used only for this purpose 'When the end ear 5 is cut after melt welding, the end ear is used To minimize metal loss. Note that in both 2a and 2b, the melt welded joint is close to the side boundary of the platinum sheet. BRIEF DESCRIPTION OF THE DRAWINGS The present invention will be more fully understood, and further advantages will become apparent from the <RTIgt; 28-201249575 Figure 1 shows a sheet placed on a bracket with chamfered edges; Figures 2a and 2b show a sheet arranged as a tubular article after a melt welding step.