1263681 ⑴ 玖 '發明說明 【發明所屬之技術領域】 本發明係有關鎂合金之成形方法，係將鎂合金鑄造 並將該鑄造品鍛造成所欲形狀者。 【先前技術】 由於鎂（Mg )之比重1 . 8，較作爲輕量金屬代表其比 重爲2.7之銘（A1 )更小’因此鎂合金非常輕。而且鍾合 金之比鋼性較銘合金爲尚’熱傳導性亦優越，因此可作爲 電器、電子機器之外框、零件之構成材料廣泛使用。 然而，由於鎂合金爲難加工性之物，有不易成形爲所 欲形狀之缺點。亦即因鎂合金之凝固潛熱小凝固速度快而 鑄造困難，且所得鑄造品有容易產生巢紋或水紋般缺陷之 缺點。因此，特別是重視外觀之製品其良率降低，且由於 必須將缺陷施予油灰處理而有成本提高之問題。由於鎂合 金爲最密六方晶型而延性低，將板材或棒材施予壓力或鍛 造加工之際必須於3 00-5 00 °C之高溫下進行，因此有加工 速度遲緩、步驟增多、鑄模壽命短等問題。 爲解決此種鎂合金難加工性之問題，日本特開平7-2 24 3 44號公報揭示於將其組成爲鋁含量6.2-7.6重量％之AZ 系鎂合金連續鑄造而獲得小合金塊之步驟中，藉由添加微 細化劑及/或控制冷卻速度而使小合金塊之平均結晶粒徑 成爲200 μιη以下，並將該小合金塊鍛造而製造大型零件之 方法。該公報亦揭示加工成爲最終製品形狀後，藉由組合 -7- (2) 1263681 溶體化處理與T6熱處理，使平均結晶粒徑成爲50 μηι以下 而提局耐触性。 另一方面，日本特開200 1 -294966號公報揭示藉由壓 鑄法或觸變模鑄成形機使鎂合金成形爲板狀，將該板材於 常溫壓延賦予應變性後，於3 5 0 - 4 0 0 °C加熱使結晶再結晶 化，藉由使結晶粒徑微細化至0. 1-30 μηι而提昇延性，並 將延性提昇之板材施予加壓加工或鍛造而成形之方法。又 ，曰本特開200 1 - 1 70734號公報及同公報1 7073 6號揭示， 將鎂合金之板材鍛造成型，藉粗鍛造與最後加工鍛造之多 個步驟使成形爲其高度爲主要部分厚度之7倍或10倍以下 之iff造品之方法 ° 然而，以鎂合金成形爲複雜且形狀精密之零件時，如 曰本特開平7-2243 44號公報所揭示，由小合金塊鍛造之方 法其形狀、厚度方面有其限度，另一方面，如日本特開 200 1 -294966號公報、同公報1 7073 4號及同公報1 70 73 6號 所揭示，由鎂合金之板材成形之方法，雖可製造較薄零件 ，但欲將該板材施予加壓加工或鍛造而獲得複雜且形狀精 密之成形品則甚爲困難。 近年來對有關鎂合金與鋁合金同樣之超塑性之表現機 制已很淸楚，顯示藉由使結晶粒徑微細化而可在高應變速 度下加工之可能性（例如「鎂技術便覽」第1 1 9- 1 25頁） 〇 一般而言，將合金成形爲複雜且精密之形狀時，以使 用如壓鑄法之射出速度，亦即充塡速度快之鑄造法爲佳。 -8- (3) 1263681 然而’如如述般由於錢合金易凝固’使用壓纟尋法等纟尋造法 易產生水紋，且因視形狀而難以充塡至鑄模之各角落，而 使成形品之大小、厚度受限。此外，若射出速度增快則鑄 液中易捲入空氣或氣體而產生巢紋，而有物性可性度之問 題。 另一方面，將該板材加壓加工時雖可成形爲與板材寬 度同大之製品，但由於鎂合金爲延性低且難加工性者，欲 形成複雜之形狀，例如欲同樣鑄造形成鑄造品甚爲困難。 就合金組成方面而言，鎂合金之鑄造性與展延性爲表 裡關係’鑄造材可選擇因鋁含量多其融熔溫度降低而容易 鑄造之AZ9 1、AM50、AM60材等使用，又，壓鑄•鍛造材 可選擇鋁含量少而延性高之AZ 3 1材使用。耐蝕性方面則 鋁含量多者耐蝕性優越。因此與AZ 9 1材相較AZ 3 1材之耐 鈾性較差，此亦爲AZ3 1材用途狹窄理由之一。 【發明內容】 本發明有鑑於上述以往之實況，其目的在提供鎂合金 之成形方法，係於可鑄造且鍛造性優越之鎂合金組成中， 藉由組合鑄造與鍛造使鎂合金成形，並以高良率製造具有 複雑而精密之形狀，且物性可信度高，耐蝕性亦充分足夠 之製品 ° 本發明係有關： 1 . 一種鎂合金之成形方法，其特徵爲將鋁含量爲2-1 〇質量。/Q之鎮合金鑄造而獲得結晶粒徑3 〇 μ m以下之鑄造 (4) 1263681 品，將該鑄造品以其組成之固溶溫度與固相線範圍之溫度 進行溶體化處理後，鍛造而得結晶粒徑1 〇 μ m以下之鍛造 品，再將該鍛造品進一步鍛造成所欲之形狀者。 2-上述項1之鎂合金之成形方法，其中，該鎂合金之 鋁含量爲2.5 - 6質量％者。 3 ·上述1或2項之鎂合金之成形方法，其中，該鑄造 係以壓鑄法或觸變模鑄法進行者。 4. 上述1至3項中任一項之鎂合金之成形方法，其中 ，該溶體化處理係於3 8 0至4 4 0 °C下進行1 - 2 4小時者。 5. 上述1至4項中任一項之鎂合金之成形方法，其中 ，係於Z値爲109-1013之應變速度及溫度條件下進行鍛造而 得結晶粒徑1 〇 μιη以下之結晶粒微細化鍛造品者。 6. 上述1至5項中任一*項之錶合金之成形方法，其中 ，結晶粒微細化鍛造品係於Ζ値爲1 013之應變速度及溫度 條件下锻造成爲所欲形狀者。 7. —種鎂合金之成形方法，其特徵爲將鋁含量爲2_ 1 〇質量％之鎂合金鑄造而獲得結晶粒徑1 Ο μ m以下之鑄造 品，將該鑄造品以其組成之固溶溫度與固相線範圍之溫度 進行溶體化處理後，鍛造成所欲之形狀者。 8 ·上述桌7項之鎂合金之成形方法，其中，該鎂合金 之銘含量爲2-6質量％者。 9.上述第7或8項之鎂合金之成形方法，其中，該鏡 造係以壓鑄法進行者。 10·上述第7至9項中任一項之鎂合金之成形方法，其 -10- (5) 1263681 中’該溶體化處理係於38〇至44〇°c下進行1-24小時者。 1 1.上述第7至1 0項中任一項之鎂合金之成形方法， 其中’係於Z値小於1 0 3之應變速度及溫度條件下進行鍛 造者。 如上述第1項之鎂合金之成形方法，其特徵爲將鋁含 量爲2_10質量％之鍾合金鑄造而得結晶粒徑30 μιη以下之 f尋造品’再將該鑄造品於其組成之固溶溫度與固相線範 圍之溫度進行溶體化處理後，鍛造而得結晶粒徑0 μιηΗ 下之鍛造品，然後再將該鍛造品進一步鍛造成所欲之形 狀。 將藉由鑄造作成結晶粒徑3 0 μιη以下之鑄造品施予溶 體化處理時，則鑄造時原來形成之粗大且脆弱晶界之第2 相粒子消失而伸展性增大，塑性加工性提昇。藉由此種溶 體化處理而鍛造塑性加工性提昇之鑄造品，可藉由鍛造使 動態再結晶而使結晶粒徑微細化至1 0 μιη以下，而進一步 提高其鍛造成形性。因此，以第1項之方法，將藉由鑄造 而成爲結晶粒徑3 0 μιη以下之鑄造品施予溶體化處理，然 後藉由鍛造使結晶粒徑成爲10 μιη以下，再進一步鍛造成 所欲之形狀。 於該方法中，鎂合金之鋁含量以2.5 - 6質量％爲佳，而 鑄造係以壓鑄法或觸變模鑄法進行爲佳。又，溶體化處理 以於3 80至440°C下進行1-24小時爲佳，溶體化處理後爲使 結晶粒微細化之鍛造及其後爲成形之鍛造以於Z値1 〇 9 - 1 〇13 之應變速度及溫度條件下進行爲佳。 -11 - (6) 1263681 上述第7項之鎂合金之成形方法，其特徵爲將鋁含量 爲2_ 10質量％之鎂合金鑄造而獲得結晶粒徑10 μιη以下之 鑄造品，再將該鑄造品以其組成之固溶溫度與固相線範圍 之溫度進行溶體化處理，然後鍛造成所欲之形狀。 將藉由鑄造而成爲結晶粒徑1 0 μιη以下之鑄造品施予 溶體化處理時，雖結晶粒粗大化，但鑄造時形成之粗大且 脆弱晶界之第2相粒子消失而伸展性增大，塑性加工性提 昇。藉由鍛造此種經溶體化處理而塑性加工性提昇之鑄造 品，可成形爲所欲之形狀。因此，以上述第7項之方法’ 將藉由鑄造而製得之結晶粒徑1 0 μ m以下之鑄造品施予 溶體化處理，然後藉由鍛造製成所欲之形狀。 於該方法中，鎂合金之鋁含量以2 - 6質量％爲佳，而 鑄造係以壓鑄法或觸變模鑄法進行爲佳。又，溶體化處理 以於3 8 0至4 4 0 °C下進行1 - 2 4小時爲佳，而其後爲了成形之 鍛造以於Z値小於1 〇 13之應變速度及溫度之條件下進行爲 佳。 Z値係指表示溫度與應變速度之關係之溫度補償應變 速度，係一般常用於表示達到流動應力之溫度與應變速度 之效果關係式之吉諾·霍落蒙（Zener-Hollomon )參數， 可以下述式（I)定義之。 Ζ= ε fexp ( Q/RT ) ........ ( I ) 此處， £ \應變速度（sec·1 ) Q :晶格擴散活性化能 -12 - (7) 1263681 R:氣體常數 T :絕對溫度 Q値因無法求得錢合金之値一*般係使用純錢之1 j 5千 焦耳/莫耳。 【實施方式】 下文詳細說明本發明鎂合金成形方法之實施方式。 首先說明上述第1項之鎂合金成形方法之實施方式。 以上述第1項之方法，先將鋁含量爲2- 1 0質量％之鎂 合金鑄造而獲得結晶粒徑3 Ο μιη以下之鑄造品。 該鎂合金之鋁含量若小於2質量％則成爲耐鈾性低劣 之物，且因融熔溫度變高而不適宜鑄造。鎂合金之鋁含量 若大於1 〇質量％則藉由後續之溶體化處理無法充分提高塑 性加工性，而無法獲得鍛造性優越之溶體化處理品。因此 ，鍾合金之錦含量爲2-1〇質量％，較好爲2.5-6質量％。 此種錶合金之鏡造法並無特別限制，但爲獲得結晶粒 徑3 Ο μηι以下之鑄造品，以採用冷卻•凝固速度較快，且 可將結晶粒微細化之壓鑄法或觸變模鑄法佳。 亦即，重力鑄造法一般係視產品厚度而融熔鎂合金之 凝固緩慢，因此於冷卻•凝固期間結晶成長而結晶粒徑粗 大達20 0 μηι，而如壓鑄法或觸變模鑄法，則係將鑄模內融 熔或半融熔狀態之鑄液射出之鑄造法，其冷卻•凝固速度 快因此結晶粒微細化，而可鑄造成爲結晶粒徑3 0 μιη以下 -13- (8) 1263681 鑄造品以結晶粒徑小者爲佳，3 Ο μιη以下即佳，視採 用之鑄造法及合金組成一般係鑄造成爲結晶粒徑1 5 -3 0 μ m 者。 藉由鑄造而得之結晶粒徑3 0 μιη以下之鑄造品，繼續 進行溶體化處理。 溶體化處理溫度係於其組成之固溶溫度與固相線範圍 之溫度即可，最適溫度爲38〇至43 〇°C。溶體化處理溫度小 於固溶溫度或小於3 8 〇 °c，則因析出鋁或鎂之巨大化合物 而妨礙塑性加工性，若超過其組成之固溶溫度或超過43 0 °C，則產生液相而妨礙塑性加工性。溶體化處理時間以1 -24小時爲宜，溫度低時以較長時間，溫度高時以較短時間 爲佳。藉由溶體化處理則析出於母相α相之結晶晶界的/5 相溶解於母相，雖母相之結晶粒粗大化但藉由減少阻礙塑 性加工性之晶界滑動之/5相可獲得提高加工性之效果。 溶體化處理後’進行鍛造而獲得結晶粒徑1 〇 μπι以下 之鍛造品（下文，亦將此用於結晶粒微細化之鍛造稱爲「 結晶粒微細化鍛造」），再將該锻造品锻造成爲所欲之形 狀而獲得製品（下文’亦將此用於鍛造成形爲所欲形狀之 鍛造稱爲「成形鍛造」）。 結晶粒微細化鍛造係藉由動態再結晶化將鑄造品之結 晶粒微細化者，該結晶粒微細化鍛造或成形鍛造均需視鎂 合金之組成而於可鍛造加工之條件範圍內進行。 結晶粒微細化鍛造之條件雖視鎂合金之組成而異，但 以ζ値爲1 〇9 -1 〇13之範圍，較好爲1 〇1 ^ -1 〇13之範圍的應變速 -14- (9) 1263681 度及溫度條件下進行爲佳。 又，成形鍛造之條件雖亦視鎂合金之組成而異， Z値爲1 013以下，較好爲1 08 -1 0 13，更好爲1 〇9 -1 012之 的應變速度及溫度條件下進行爲佳。 結晶粒微細化鍛造及成形鍛造之任一者其鍛造條 爲上述較佳Z値之範圍以外，則有產生破損、裂痕等 而不能鍛造之情況。 一般情況，結晶粒微細化鍛造係視合金組成而設 件，以應變速度lO^-lOdsec·1、溫度200-5 00 °C之範 上述Z値之適當範圍，成形鍛造係視合金組成而設定 ，以應變速度lO — LlOisec·1、溫度200-400 t之範圍 述Z値之適當範圍。 藉由結晶粒微細化鍛造使結晶粒徑成爲1 0 μ m以 並藉由鍛造改善塑性加工性，而可成形鍛造。該結晶 爲1 0 μιη以下即可，一般而言係施行結晶粒徑成爲約 μπι之結晶粒微細化鍛造。 繼之說明上述弟7項之鎂合金成形方法之實施方3 上述第7項之方法係先將鋁含量爲2-1 0質量％之 金鑄造而獲得結晶粒怪1 0 μ m以下之鑄造品。 該鎂合金之銘含量若小於2質量％則成爲耐蝕性 之物。鎂合金之鋁含量若大於1 0質量％則藉由後續之 化處理無法充分提高塑性加工性，而無法獲得鍛造性 之溶體化處理品。因此，鎂合金之鋁含量爲2-10質量 較好爲2 - 6質量％。 但以 範圍 件若 缺陷 定條 圍爲 條件 爲上 下， 粒徑 1-10 鎂合 低劣 溶體 優越 %， -15- (10) 1263681 又，所用鎂合金之鋁以外之其他成分含量係與上述第 1項之方法中所述者相同。 此種鎂合金之鑄造法爲獲得結晶粒徑〗〇 μηι以下之鏡 造品，以採用冷卻•凝固速度非常迅速，可將結晶粒微細 化之壓鑄法較佳。 鑄造品之結晶粒徑雖以小者爲佳，而1 〇 μ 1Ή以下即可 ’視採用之合金組成，一般係鑄造成爲5 - 1 〇 μ m之結晶粒 徑。 藉由鑄造而獲得之結晶粒徑1 0 μηι以下之鑄造品，在 於其組成之固溶溫度與固相線範圍之溫度進行溶體化處王里 ，以提高加工性。該溶體化處理條件係與上述第1項方法 之溶體化處理同樣理由，以3 8 0至4 3 0 °C，1 - 2 4小時爲佳， 溶體化處理後再鍛造成爲所欲之形狀而獲得製品。 該鍛造亦與上述第1項之方法同樣，必須視鎂合金之 組成而於可鍛造加工之條件範圍進行。 鍛造之條件雖亦視鎂合金之組成而異，但以Z値小於 1 0 13之範圍，較好於z値爲1 0 6 -1 0 12之範圍的應變速度及溫 度條件下進行’ Z値爲1013以上則有產生破損、裂痕等缺 陷而不能鍛造之情況。 一般情況，上述鍛造係視合金組成而設定條件，以應 變速度lO-llO^secT1、溫度200-500 °C之範圍可使上述z値 爲適當範圍。 〔實施例〕 -16- (11) 1263681 下文列舉實施例具體說明本發明 又’於下列貫施例中所使用之鏡合金紅’係於市售之 AZ 9 1合金錠中添加鎂與鋅進行成分調整而製作者，據此 製作AZ8 1-AZ2 1組成之鎂合金錠。所使用之ΑΖΘ1合金錠與 所製作之合金錠之成分分析結果示於表1 ° 表1 合金錠之成分分析結果 （質量％) _ 合金 錠 A1 Zn Μη Si C u Fe Ni Be AZ9 1 8.9 0.70 0.2 1 0.3 10 0.0400 0.0020 0.0004 0.0008 AZ8 1 7.6 0.70 0.30 0.025 0.0010 0.0017 t r 0.0034 AZ7 1 6.9 0.72 0.24 0.024 0.0011 0.0003 tr 0.0019 AZ6 1 5.7 0.79 0.30 0.024 0.0010 0.0029 tr 0.0026 AZ5 1 4.8 0.78 0.29 0.018 0.0009 0.0013 tr 0.0022 AZ4 1 3 . 6 0.68 0.27 0.013 0.0008 0.0012 t r 0.0014 AZ3 1 2.6 0.60 0.28 0.010 0.0004 tr t r 0.0016 AZ2 1 2.1 0.83 0.28 0.003 0.0052 tr t r 0.0030 實施例1 (:1 )鑄造及溶體化處理 將AZ 9 1 - AZ 2 1之合金錠硏削作成觸變模鑄用晶圓以供 鑄造。以日本製鋼所製觸變模鑄成形機45 0 ’設定於 空打條件下射出速度最高爲4m/sec，以鑄模溫度設定爲 250 °C之縱181mm X寬255mm X高l〇mm有底無盡之箱型隹《 模製得厚度1.5 mm之鑄造品。又，鑄造時’因各合金淀之 -17- (12) 1263681 融點不同，係於調整機筒與噴嘴溫度，同時探討成形可能 之條件下進行鑄造。各合金鑄造時之機筒先端溫度示於表 2 〇 表2 觸變模鑄藥造之機筒先端温度 合金 __ 溫度（°C ) AZ9 1 620 AZ8 1 6 18 AZ7 1 _ 6 19 AZ6 1 624 AZ5 1 63 7 AZ4 1 640 AZ3 1 63 8 其結果爲AZ9 1至AZ3 1可進行鑄造，而AZ21熔點爲 64 5 °C，於成形機之加熱界線內不融熔而無法鑄造。因此 ’咸認AZ系合金之觸變模鑄成形機之鑄造界線爲鋁含量 2.5% 〇 觸變f吴__造所得纟尋造品結晶粒徑之測定，係自各鑄 造品之中央部位採樣，包埋於樹脂並硏磨後，視樣品組成 以古液酸或乙酸系蝕刻劑進行飩刻，以5 00倍電子顯微鏡 攝影’依據JIS GO522之「鋼塊結晶粒度試驗法」之切片 法測定，求得之粒徑爲1 . 7 4倍。 又’爲確認溶體化處理之效果，將各鑄造品於4 3 0 °C 熱處理1小時後，同樣測定結晶粒徑。 -18- 1263681 (13) 此等結果示於表3或第1圖 觸變^造之，結晶_立平签 合金 --- 結晶粒徑（tum) -----~" 溶體化處理_ 溶體化處理後 — AZ9 1 13.1 28.3 — AZ8 1 12.3 19.1 — AZ7 1 10.2 16.4 一 AZ6 1 13.1 24.6 — AZ5 1 10.1 13.7 — AZ4 1 12.4 20.2 — AZ3 1 10.5 17.9 由表3及第1圖可知，溶體化處理前之結晶粒徑雖組成 不同差異並不大，經溶體化處理而結晶粒徑粗大化。此係 進行溶體化處理時，存在於晶界之Θ相溶解於母相之α相 而使結晶粒粗大化。咸認該結晶粒徑係鑄液急冷而凝固速 度快者粒徑小，結果如下。亦即，鋁含量由ΑΖ9 1至ΑΖ 3 1 減少而熔點上升。因此，由於提高成形機先端之機筒溫度 ’藉由鑄液溫度與鑄模之溫度差可達到急冷效果，而有自 該溫度差小之AZW之結晶粒徑28μηι，至溫度差大之ΑΖ51 之結晶粒徑1 4 μιη，結晶粒徑有變小之傾向。然而，若爲 ΑΖ 4 1、ΑΖ 3 1時貝[J相反的由於高溫之鑄液具有延遲冷谷ρ之 作用’而成爲結晶粒徑較大之1 8 - 2 Ο μ m。 又，爲檢視溶體化處理品之塑性加工性，自各鑄造品 -19- 1263681 (14)1263681 (1) 发明 'Invention> Technical Field of the Invention The present invention relates to a method for forming a magnesium alloy by casting a magnesium alloy and forging the cast product into a desired shape. [Prior Art] Since the specific gravity of magnesium (Mg) is 1.8, it is smaller than the light weight of metal (A1) which is 2.7. Therefore, the magnesium alloy is very light. Moreover, the ratio of the alloy to the alloy is better than that of the alloy. The thermal conductivity is also excellent. Therefore, it can be widely used as a constituent material for electrical and electronic equipment. However, since the magnesium alloy is difficult to process, it has a drawback that it is not easily formed into a desired shape. That is, since the solidification latent heat of the magnesium alloy has a small solidification speed and is difficult to cast, the obtained cast product has a drawback that it is liable to cause nesting or water-grain-like defects. Therefore, in particular, the product which pays attention to the appearance has a low yield, and there is a problem that the cost is increased because the defect must be applied to the putty treatment. Since the magnesium alloy is the densest hexagonal crystal form and the ductility is low, the plate or bar must be applied at a high temperature of 300 to 00 °C when it is subjected to pressure or forging processing, so that the processing speed is slow, the steps are increased, and the mold is molded. Short life and other issues. In order to solve the problem of the intractability of the magnesium alloy, Japanese Laid-Open Patent Publication No. Hei 7-2 24 3 44 discloses a step of continuously casting a small alloy block by continuously casting an AZ-based magnesium alloy having an aluminum content of 6.2 to 7.6% by weight. In the meantime, a method of producing a large-sized part by forging a small alloy ingot by adding a refining agent and/or controlling a cooling rate to have an average crystal grain size of 200 μm or less. This publication also discloses that after processing into the final product shape, the combination of -7-(2) 1263681 solution treatment and T6 heat treatment makes the average crystal grain size 50 μηι or less to improve the contact resistance. On the other hand, Japanese Laid-Open Patent Publication No. 2001-294966 discloses that a magnesium alloy is formed into a plate shape by a die casting method or a thixotropic die casting machine, and the plate material is subjected to room temperature rolling to impart strain, and then is subjected to 3 5 0 - 4 0 0 ° C heating to recrystallize the crystal, by making the crystal grain size to 0. 1-30 μηι to improve the ductility, and the ductility-enhanced sheet is subjected to press processing or forging to form. Further, in Japanese Unexamined Patent Publication No. Publication No. Publication No. Publication No. Publication No. No. No. No. No. No. No. No. No. No. No. No. No. No. No. No. Nos. A method of iff manufacturing of 7 times or less. However, when a magnesium alloy is formed into a complicated and precise shape, the method of forging from a small alloy block is disclosed in Japanese Patent Laid-Open Publication No. Hei 7-2243 44. There is a limit to the shape and the thickness thereof. On the other hand, a method of forming a sheet of a magnesium alloy, as disclosed in Japanese Laid-Open Patent Publication No. 2001-294966, No. 7,073, 4 Although it is possible to manufacture thinner parts, it is difficult to apply the sheet to press working or forging to obtain a molded article having a complicated shape and precision. In recent years, the performance mechanism of superplasticity similar to that of magnesium alloys and aluminum alloys has been very difficult, showing the possibility of processing at high strain rates by making the crystal grain size fine (for example, "Magnesium Technology Handbook" No. 1 1 9- 1 25) In general, when forming an alloy into a complex and precise shape, it is preferable to use a casting method such as a die casting method, that is, a casting method in which the charging speed is fast. -8- (3) 1263681 However, as described above, since the alloy is easy to solidify, it is easy to produce water marks by using the pressure-seeking method, etc., and it is difficult to fill the corners of the mold because of the shape. The size and thickness of the molded article are limited. In addition, if the injection speed is increased, the casting liquid is likely to be entrapped with air or gas to form a nest, and there is a problem of physical properties. On the other hand, when the sheet material is subjected to press working, it can be formed into a product having the same width as the sheet material. However, since the magnesium alloy is low in ductility and difficult to process, it is desired to form a complicated shape, for example, to cast a casting product. For the sake of difficulty. In terms of alloy composition, the castability and ductility of magnesium alloys are in the relationship between 'the casting materials can be selected because of the aluminum content and the melting temperature is lowered, and the AZ9 1, AM50, AM60 materials, etc., which are easy to be cast, are used. • Forged materials can be selected from AZ 3 1 with low aluminum content and high ductility. In terms of corrosion resistance, the aluminum content is superior in corrosion resistance. Therefore, compared with AZ 9 1 material, the uranium resistance of AZ 3 1 material is poor, which is one of the reasons for the narrow use of AZ3 1 material. SUMMARY OF THE INVENTION The present invention has been made in view of the above-described conventional circumstances, and an object thereof is to provide a method for forming a magnesium alloy by molding a magnesium alloy by combination casting and forging in a magnesium alloy composition which is excellent in castability and forgeability, and The invention relates to a method for forming a magnesium alloy, which has a high-yield shape and a precise shape, and has high reliability and high corrosion resistance. The invention relates to: 1. A method for forming a magnesium alloy, characterized in that the aluminum content is 2-1 〇 quality. /Q town alloy casting to obtain a casting (4) 1263681 with a crystal grain size of 3 〇μm or less. The cast product is solutionized by the solution temperature of the composition and the temperature of the solidus line range, and then forged. The forged product having a crystal grain size of 1 μm or less is obtained, and the forged product is further forged into a desired shape. The method of forming a magnesium alloy according to item 1, wherein the magnesium alloy has an aluminum content of from 2.5 to 6% by mass. 3. The method for forming a magnesium alloy according to the above item 1 or 2, wherein the casting is carried out by a die casting method or a thixotropic molding method. 4. The method for forming a magnesium alloy according to any one of the above items 1 to 3, wherein the solution treatment is carried out at 380 to 4400 ° C for 1 to 24 hours. 5. The method for forming a magnesium alloy according to any one of the above items 1 to 4, wherein the crystal grain having a crystal grain size of 1 〇μηη or less is obtained by forging at a strain rate and a temperature of 109 to 1013. Forging products. 6. The method for forming an alloy according to any one of the above items 1 to 5, wherein the crystal grain refining forged product is forged into a desired shape at a strain rate and temperature of 1 013. 7. A method for forming a magnesium alloy, characterized in that a magnesium alloy having an aluminum content of 2 to 1% by mass is cast to obtain a cast product having a crystal grain size of 1 Ο μ m or less, and the cast product is dissolved in a composition thereof. After the temperature and the temperature of the solidus line are melted, the desired shape is forged. 8. The method for forming a magnesium alloy according to the above item 7, wherein the content of the magnesium alloy is 2-6 mass%. 9. The method of forming a magnesium alloy according to Item 7 or 8, wherein the mirroring is carried out by a die casting method. 10. The method for forming a magnesium alloy according to any one of items 7 to 9 above, wherein in the -10-(5) 1263681, the solution treatment is carried out at 38 to 44 ° C for 1 to 24 hours. . 1 1. The method for forming a magnesium alloy according to any one of the items 7 to 10 above, wherein the one is forged at a strain rate and a temperature of Z 値 less than 130. The method for forming a magnesium alloy according to the above item 1, characterized in that a clock alloy having an aluminum content of 2 to 10% by mass is cast to obtain a f-product of a crystal grain size of 30 μm or less, and the cast product is solidified in its composition. After the solution temperature and the solidus temperature range are melted, the forged product having a crystal grain size of 0 μm is forged, and the forged product is further forged into a desired shape. When the cast product having a crystal grain size of 30 μm or less is cast by casting, the second phase particles which are originally formed at the time of casting and the fragile grain boundaries are eliminated, the stretchability is increased, and the plastic workability is improved. By such a solution treatment, the cast product having improved plastic workability is forged, and the crystal grain size can be made finer to 10 μm or less by forging re-crystallization, thereby further improving the forge formability. Therefore, in the method of the first item, a cast product having a crystal grain size of 30 μm or less by casting is subjected to a solution treatment, and then the crystal grain size is 10 μm or less by forging, and further forging is desired. shape. In the method, the aluminum content of the magnesium alloy is preferably from 2.5 to 6% by mass, and the casting is preferably carried out by die casting or thixotropic molding. Further, the solution treatment is preferably carried out at 380 to 440 ° C for 1 to 24 hours, and after the solution treatment, the forging of the crystal grains is followed by the forging of the crystal grains, and then the forging is performed for Z 値 1 〇 9 - 1 〇 13 is preferably carried out under strain rate and temperature conditions. -11 - (6) 1263681 The method for forming a magnesium alloy according to the above item 7, characterized in that a magnesium alloy having an aluminum content of 2 to 10% by mass is cast to obtain a casting having a crystal grain size of 10 μηη or less, and the casting product is further obtained. It is solutionized by the solution temperature of the composition and the temperature of the solidus line, and then forged into a desired shape. When the cast product having a crystal grain size of 10 μm or less by casting is subjected to a solution treatment, the crystal grains are coarsened, but the second phase particles which are formed at the time of casting and which are coarse and fragile grain boundaries disappear, and the stretchability increases. Plastic workability is improved. A cast product having improved plastic workability by forging such a solution treatment can be formed into a desired shape. Therefore, the cast product having a crystal grain size of 10 μm or less obtained by casting is subjected to a solution treatment by the method of the above item 7, and then the desired shape is formed by forging. In the method, the aluminum content of the magnesium alloy is preferably from 2 to 6% by mass, and the casting is preferably carried out by die casting or thixotropic molding. Further, the solution treatment is preferably carried out at 380 to 440 ° C for 1 to 24 hours, and thereafter forging for forming so that the Z 値 is less than 1 〇 13 at the strain rate and temperature. It is better to carry out. Z値 is a temperature-compensated strain rate indicating the relationship between temperature and strain rate. It is commonly used to represent the Zener-Hollomon parameter for the relationship between the temperature and strain rate at which the flow stress is reached. Described in the formula (I). Ζ = ε fexp ( Q/RT ) ........ ( I ) Here, £ \ strain rate (sec·1 ) Q : lattice diffusion activation energy -12 - (7) 1263681 R: gas Constant T: Absolute temperature Q値 can not be obtained because of the use of pure money 1 j 5 kJ / Moule. [Embodiment] Hereinafter, embodiments of the magnesium alloy forming method of the present invention will be described in detail. First, an embodiment of the magnesium alloy forming method of the above first item will be described. In the method of the above first item, a magnesium alloy having an aluminum content of 2 to 10% by mass is first cast to obtain a cast product having a crystal grain size of 3 Ο μηη or less. When the aluminum content of the magnesium alloy is less than 2% by mass, it is inferior in uranium resistance, and it is not suitable for casting because the melting temperature is high. When the aluminum content of the magnesium alloy is more than 1% by mass, the plastic workability cannot be sufficiently improved by the subsequent solution treatment, and the solution processed product excellent in forgeability cannot be obtained. Therefore, the content of the alloy of the bell alloy is 2-1 〇 mass%, preferably 2.5 -6 mass%. The mirror forming method of the alloy is not particularly limited, but in order to obtain a cast product having a crystal grain size of 3 Ο μηι or less, a die casting method or a thixotropic mold which has a fast cooling and solidification speed and which can refine the crystal grains can be used. Casting is good. That is to say, the gravity casting method generally has a slow solidification of the molten magnesium alloy depending on the thickness of the product, so that the crystal grows during cooling and solidification and the crystal grain size is as large as 20 0 μηι, and as in the case of die casting or thixotropic molding, It is a casting method in which a casting liquid in a molten or semi-molten state is injected in a mold, and the cooling and solidification speed is fast, so that the crystal grains are refined, and can be cast into a crystal grain size of 3 0 μηη or less-13-(8) 1263681 casting It is preferable that the product has a small crystal grain size, and it is preferably 3 Ο μιη or less, and the casting method and the alloy composition are generally cast to have a crystal grain size of 15 - 30 μm. The cast product having a crystal grain size of 30 μm or less obtained by casting is further subjected to a solution treatment. The solution treatment temperature is preferably a solution temperature of the composition and a temperature in the solidus range, and the optimum temperature is 38 〇 to 43 〇 ° C. When the solution treatment temperature is less than the solid solution temperature or less than 3 8 〇 ° C, the plasticity is inhibited by the precipitation of a large compound of aluminum or magnesium, and if it exceeds the solid solution temperature of the composition or exceeds 43 ° C, the liquid is produced. This hinders plastic workability. The solution treatment time is preferably from 1 to 24 hours, with a longer time at a lower temperature and a shorter time at a higher temperature. By the solution treatment, the /5 phase of the crystal grain boundary precipitated in the mother phase α phase is dissolved in the parent phase, and although the crystal grains of the parent phase are coarsened, the λ phase of the grain boundary sliding which hinders the plastic workability is reduced. The effect of improving workability can be obtained. After the solution treatment, 'forging is performed to obtain a forged product having a crystal grain size of 1 μm or less (hereinafter, the forging for crystal grain refinement is also referred to as "fine grain forging"), and the forged product is further The product is obtained by forging into a desired shape (hereinafter, 'forging for the shape of the desired shape is referred to as "forming forging"). The grain refinement forging is a process in which the grain of the cast product is refined by dynamic recrystallization, and the grain grain fine forging or forming forging is performed within the conditions of the forgeable processing depending on the composition of the magnesium alloy. Although the conditions for the fine grain forging of the crystal grains vary depending on the composition of the magnesium alloy, the range of 1 〇9 -1 〇13, preferably 1 〇1 ^ -1 〇13, is required. (9) 1263681 degrees and temperature conditions are preferred. Moreover, the conditions of the forming forging vary depending on the composition of the magnesium alloy, and Z値 is 1 013 or less, preferably 1 08 -1 0 13, more preferably 1 〇9 -1 012 under strain rate and temperature conditions. It is better to carry out. In the case of any of the fine grain forging and forming forging of the crystal grain, the forged bar may be damaged or cracked, and may not be forged. In general, the crystal grain is refined and the forging is based on the composition of the alloy, and is set at a strain rate of lO^-lOdsec·1, a temperature of 200-5 00 °C, and an appropriate range of the above-mentioned Z値, and is formed by forming a forged alloy composition. The appropriate range of Z値 is described in the range of strain rate lO - LlOisec·1, temperature 200-400 t. Forming forging can be carried out by refining the crystal grains to make the crystal grain size 10 μm and improving the plastic workability by forging. The crystal may be 10 μm or less, and generally, a crystal grain having a crystal grain size of about μ μm is finely forged. Next, the method for the magnesium alloy forming method of the above-mentioned seventh item is described. The method of the above item 7 is to cast a gold having an aluminum content of 2-1% by mass to obtain a casting product having a crystal grain size of 10 μm or less. . When the content of the magnesium alloy is less than 2% by mass, the corrosion resistance is obtained. When the aluminum content of the magnesium alloy is more than 10% by mass, the plastic workability cannot be sufficiently improved by the subsequent treatment, and the forged solution product cannot be obtained. Therefore, the magnesium alloy has an aluminum content of 2 to 10% by mass, preferably 2 to 6% by mass. However, if the range is limited by the defect, the particle size is 1-10. The magnesium alloy is inferior to the poor solution. -15- (10) 1263681 The content of the other components other than the aluminum alloy used is the same as the above. The method described in the item 1 is the same. The casting method of such a magnesium alloy is a mirror product having a crystal grain size of 〇 μηι or less, and a die casting method in which the cooling and solidification rate is very rapid and the crystal grains can be refined is preferable. The crystal grain size of the cast product is preferably small, and 1 〇 μ 1 Ή or less ‘ depending on the alloy composition used, it is generally cast to a crystal grain size of 5 - 1 〇 μ m. A cast product having a crystal grain size of 10 μm or less obtained by casting is melted at a temperature at a solid solution temperature and a solidus temperature range of the composition to improve workability. The solution treatment conditions are preferably the same as the solution treatment of the first method, and are preferably 380 to 430 ° C for 1 to 24 hours, and then forged after the solution treatment. The shape is obtained to obtain an article. This forging is also carried out in the same conditions as in the above-mentioned item 1, depending on the composition of the magnesium alloy and in the range of conditions for the forging process. The conditions for forging vary depending on the composition of the magnesium alloy, but the Z 値 is less than 10 13 , preferably at a strain rate and temperature range of z 値 1 0 6 -1 0 12 'Z値If it is 1013 or more, there are defects such as breakage and cracks which cannot be forged. In general, the above forging conditions are set depending on the alloy composition, and the above z 値 can be set to an appropriate range in the range of the strain rate lO-llO^secT1 and the temperature of 200-500 °C. [Examples] -16- (11) 1263681 Hereinafter, the examples are specifically described in the present invention, and the "mirror alloy red" used in the following examples is added to a commercially available AZ 9 1 alloy ingot by adding magnesium and zinc. The composition was adjusted and the producer made a magnesium alloy ingot composed of AZ8 1-AZ2 1 accordingly. The composition analysis results of the alloy 1 ingot and the alloy ingot used are shown in Table 1 ° Table 1 Composition Analysis Results (% by mass) of the alloy ingot _ Alloy ingot A1 Zn Μη Si C u Fe Ni Be AZ9 1 8.9 0.70 0.2 1 0.3 10 0.0400 0.0020 0.0004 0.0008 AZ8 1 7.6 0.70 0.30 0.025 0.0010 0.0017 tr 0.0034 AZ7 1 6.9 0.72 0.24 0.024 0.0011 0.0003 tr 0.0019 AZ6 1 5.7 0.79 0.30 0.024 0.0010 0.0029 tr 0.0026 AZ5 1 4.8 0.78 0.29 0.018 0.0009 0.0013 tr 0.0022 AZ4 1 3 6 0.68 0.27 0.013 0.0008 0.0012 tr 0.0014 AZ3 1 2.6 0.60 0.28 0.010 0.0004 tr tr 0.0016 AZ2 1 2.1 0.83 0.28 0.003 0.0052 tr tr 0.0030 Example 1 (:1) Casting and solution treatment AZ 9 1 - AZ 2 1 The alloy ingot is diced into a wafer for thixotropic die casting for casting. The Thixoforming Molding Machine 45 0 ' made by Nippon Steel Co., Ltd. is set to a maximum speed of 4 m/sec under free-running conditions, and the mold temperature is set to 250 °C. Vertical 181 mm X width 255 mm X high l〇mm endless endless Box type 隹 "Molded castings with a thickness of 1.5 mm. In addition, at the time of casting, the melting point of each alloy -17-(12) 1263681 is different, and the casting is performed under the condition that the barrel and the nozzle temperature are adjusted and the forming is possible. The temperature of the barrel tip at the time of casting of each alloy is shown in Table 2. 2 Table 2 The barrel tip temperature alloy made by thixotropic molding __ Temperature (°C) AZ9 1 620 AZ8 1 6 18 AZ7 1 _ 6 19 AZ6 1 624 AZ5 1 63 7 AZ4 1 640 AZ3 1 63 8 The result is that AZ9 1 to AZ3 1 can be cast, while AZ21 has a melting point of 64 5 °C, which does not melt in the heating boundary of the forming machine and cannot be cast. Therefore, the casting boundary of the thixotropic die-casting machine of the AZ-based alloy is 2.5% aluminum content. 〇 Thixotropy f _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ After being embedded in the resin and honed, the composition of the sample is engraved with an ochreic acid or acetic acid etchant, and is measured by a 500-fold electron microscope photography according to the slice method of "Steel Crystal Grain Size Test Method" of JIS GO522. The particle size obtained was 1.7 times. Further, in order to confirm the effect of the solution treatment, each of the cast products was heat-treated at 430 ° C for 1 hour, and then the crystal grain size was measured in the same manner. -18- 1263681 (13) These results are shown in Table 3 or Figure 1. The crystallized _ Liping alloy - crystal grain size (tum) -----~" Treatment_ After solution treatment - AZ9 1 13.1 28.3 — AZ8 1 12.3 19.1 — AZ7 1 10.2 16.4 AZ6 1 13.1 24.6 — AZ5 1 10.1 13.7 — AZ4 1 12.4 20.2 — AZ3 1 10.5 17.9 As can be seen from Table 3 and Figure 1. The crystal grain size before the solution treatment is not greatly different in composition, and the crystal grain size is coarsened by the solution treatment. When the solution is subjected to the solution treatment, the ruthenium phase existing at the grain boundary is dissolved in the α phase of the parent phase to coarsen the crystal grains. It is considered that the crystal grain size is rapidly cooled and the solidification rate is small, and the particle size is small. The results are as follows. That is, the aluminum content decreases from ΑΖ9 1 to ΑΖ 3 1 and the melting point rises. Therefore, since the barrel temperature of the tip of the forming machine is increased, the quenching effect can be achieved by the temperature difference between the temperature of the casting liquid and the mold, and the crystal grain size of the AZW which is small from the temperature difference is 28 μm, and the crystal of the temperature difference is ΑΖ51. When the particle diameter is 1 4 μm, the crystal grain size tends to be small. However, if it is ΑΖ 4 1 and ΑΖ 3 1 [ [J, the casting liquid having a high temperature has the effect of delaying the cold ρ, the larger the crystal grain size is 18 - 2 Ο μ m. In addition, in order to examine the plastic workability of the solution treated product, each casting product -19-1263681 (14)
切割拉伸試驗片，於4 2 0 °c溶體化處理1小時後，以3 Ο 0 °C 、應變速度]·〇 x 1 進行拉伸試驗，結果示於第2圖 〇 由第2圖可知，鋁含量多之AZ91至AZ71之伸展度較低 爲1 5 - 2 4 %，A Z 6 1至A Z 3 1之伸展度則爲4 0 %以上，塑性加 工性特別提高。 因此供鍛造之鑄造品之銘含量範圍，就鑄造性而言以 2.5質量％以上，就加工性而言以6質量％以下爲佳。 (2 ) 鍛造 於上述（1 )中，將以觸變模鑄法鑄造之A Z 6 1至A Z 3 1 之鏡造品於4 2 0 C ί谷體化處理1小時後，切割2 0 m m X 2 0 m m 之樣品以電爐均勻加熱，並置於預先在依表4所示之規定 鍛造溫度下保溫之鑄模內，以應變速度3 · 3 X 1 (Γ2 s e c·】之 一定條件進行鍛造。自锻造後之樣品切出試驗片，以與上 述（1 )中之相同方法測定結晶粒徑，結果示於表4。又， 將前述應變速度代入上述（I )式中求得之Z値如表4所示 。此處適用於計算之Q値爲135仟焦耳/莫耳。表4一倂記載 各樣品鍛造則（溶體化處理後）之結晶粒徑。 -20- 1263681 寸m 卜溶體化處理後(鍛造前) 結晶粒徑(μηι) 24.6 13.7 20.2 17.9 鍛造後之結晶粒徑(μιη) 350 3.3xl0'2 6.9χ109 12.9 10.0 18.8 r—H iri t—H 300 3.3xl0_2 6.7χ1010 r-H cn 卜· 10.4 14.2 250 3.3xl0_2 l.OxlO12 * <N ο 寸 寸 200 3.3χ10_2 2.7χ1013 * 关 * o f-H !' < 3.3xl0'2 1.5χ1015 * * * * 鍛造溫度(°c) Ν ω c/) 倒 Μ jM Ν ΑΖ61 AZ51 ΑΖ41 AZ31 鍛造 條件The tensile test piece was cut and dissolved at 4 20 ° C for 1 hour, and then subjected to a tensile test at 3 Ο 0 ° C and a strain rate 〇 1 x 1 . The results are shown in Fig. 2 and Fig. 2 It can be seen that the elongation of AZ91 to AZ71 having a high aluminum content is as low as 15 - 24%, and the elongation of AZ 6 1 to AZ 3 1 is more than 40%, and the plastic workability is particularly improved. Therefore, the range of the content of the cast product for forging is preferably 2.5% by mass or more in terms of castability, and preferably 6% by mass or less in terms of workability. (2) Forging in the above (1), the mirror product of AZ 6 1 to AZ 3 1 cast by thixotropic die casting is subjected to a soaking treatment at 4 2 0 C ί for 1 hour, and then cut 20 mm X The 20 mm sample was uniformly heated in an electric furnace and placed in a mold previously held at the forging temperature shown in Table 4, and forged at a strain rate of 3 · 3 X 1 (Γ2 sec·). After the test piece was cut out, the crystal grain size was measured in the same manner as in the above (1), and the results are shown in Table 4. Further, the above strain rate was substituted into the above formula (I), and Z is as shown in Table 4. As shown here, the calculated Q値 is 135 仟 joules/mole. Table 4 shows the crystal grain size of each sample forging (after solution treatment). -20- 1263681 inch m After treatment (before forging) Crystal grain size (μηι) 24.6 13.7 20.2 17.9 Crystal grain size after forging (μιη) 350 3.3xl0'2 6.9χ109 12.9 10.0 18.8 r-H iri t-H 300 3.3xl0_2 6.7χ1010 rH cn · 10.4 14.2 250 3.3xl0_2 l.OxlO12 * <N ο inch inch 200 3.3χ10_2 2.7χ1013 *off* o fH !' < 3.3xl0'2 1. 5χ1015 * * * * Forging temperature (°c) Ν ω c/) Inverted Μ jM Ν ΑΖ61 AZ51 ΑΖ41 AZ31 Forging conditions
-21 - (16) 1263681 由表4可明瞭下列各點。 亦即，發現在同一鍛造溫度下，鋁含量多之合金經 鍛造結晶有容易微細化之現象。另一方面，鋁含量多之 金在較低溫度時鍛造加工中會破損，以實驗之應變速度 相對於AZ 6 1可於3 0 0 °C以上鍛造，AZ 3 1亦可於2 0 0 °C以 鍛造，而獲得結晶粒微細化之效果。 由該結果可知’可使結晶粒徑進彳了結晶粒微細化成 可超塑性鍛造之10 μιη以下之鍛造條件爲，AZ61至AZ3] 合金爲Ζ値109-1013之範圍，較好爲101Q-1013之範圍。 選擇藉由上述鍛造，將結晶粒微細化之樣品與未充 微細化之樣品，切割2 0 m m X 2 0 m m X 1 . 5 m m厚之板狀樣 ，將該樣品插入鍛造鑄模之下模20mm x 20 mm空模中， 表5所不條件至真應變-1 . 1，以直徑3 m m、高1 0 m m之具 圓筒形凹部之上模鍛造成形爲鑄造品之形狀，鍛造加工 之鍛造性是否良好不於表5。 由 合 5 上 爲 之 分 品 依 有 時 - 22- 1263681 进'_驩^0§绷驢驢鹚飄襲 Lo^ OsJ 1 1 1 500 3.3x10'2 4.4χ107 〇 X 〇 〇 〇 〇 < 〇 〇 〇 400 3.3x10'2 9·9χ108 〇 X 〇 〇 〇 〇 X 〇 〇 <] 350 3.3x1 Ο·2 6.9χ109 〇 X 〇 〇 < 〇 X 〇 〇 X ill gg 槪 300 3.3x10'2 6.7χ1010 <] X 〇 〇 < 〇 X 〇 〇 X 200 3.3x10'2 2·7χ1013 X < < <] 〇 X 〇 〇 X 150 3.3x10'2 1·5χ1015 X X X X X X X X X X 鍛造溫度(°C) Ο C/D m m 粼 m Ν Γ Γ Γ CNJ 00 Γ CO 卜· Γ Γ ο 寸 Τ— Γ Γ Γ *τ— (£> 12.9 ο 18.8 ο Τ— CD 寸· 14.2 鍛造 條件 ΑΖ81 ΑΖ51 ΑΖ41 ΑΖ31 ^^i§nDni ^ is—1^ πππ^^ιι^^^ιό s^i-Γ -23- (18) 1263681 由表5可認知下列事實。 於晶界/3相易析出，而易阻礙晶界滑動之鋁含量多之 組成者必須以較高加工溫度，亦即以較大之Z値才能形成 鑄造品。另一方面，結晶粒徑即使超過1 〇 μ m，其合金以 較局之加工溫度亦可形成鑄造品。 然而，工業上若鑄模溫度達4 0 0 °C以上，則鑄模耐久 性不佳並不實用。雖使用耐熱性材料或經表面處理亦可改 善鑄模之高溫耐久性，但鑄模成本提高而不理想。 由此結果可知，欲成形爲所欲形狀之鍛造條件， AZ61至AZ31之合金爲Z値1013以下之範圍，而以1〇8-1〇13 之範圍爲佳。 實施例2 (1 )鑄造及溶體化處理 以壓鑄法替代實施例1之觸變模鑄法進行鑄造試驗。 使用與觸變模鑄法成形時相同成形品形狀之鑄模，合金係 直接使用於觸變模鑄成形機中所使用之同樣進料之合金錠 ’並不先作成晶圓者。使用日本東芝機械製DC650 tCLS 冷室壓鑄成形機，設定鑄液溫度70(TC，高速時之射出速 度5.0m/sec，鑄模溫度25〇 之條件依序進行鑄造。各鑄 造品之尺寸、形狀係與實施例1相同。 觸變模鑄法無法成形之ΑΖ2 1材以壓鑄法亦可進行鑄 造°此係因壓鑄法並非如觸變模鑄成形機般於成形機之機 筒內將材料熔融’而係於與成形機分開設置之給液裝置中 -24- (19) 1263681 將材料熔融，因而熔融溫度可高達7 0 (TC，而可使熔點高 之AZ2 1亦融熔之故。 各鑄造品係與實施例1同樣操作並測定溶體化處理前 後之結晶粒徑，結果示於表6及第3圖。又，溶體化處理係 於4 3 0 °C進行1小時。 表6 壓鑄鑄造品之結晶粒徑 合金 結晶粒徑（μ m ) 溶體化處理前 溶體化處理後 ΑΖ9 1 7.3 14.9 ΑΖ8 1 6.4 13.1 ΑΖ7 1 7.0 13.8 ΑΖ6 1 7.8 15.2 ΑΖ5 1 6.9 10.4 ΑΖ4 1 6.1 11.3 ΑΖ3 1 5.7 9.5 ΑΖ2 1 5.8 9.7-21 - (16) 1263681 The following points are indicated in Table 4. That is, it has been found that at the same forging temperature, the alloy having a large aluminum content is easily refined by forging crystals. On the other hand, gold with a high aluminum content will be damaged in the forging process at a lower temperature. The experimental strain rate can be forged at 300 °C or higher relative to AZ 6 1 , and AZ 3 1 can also be at 200 °. C is forged to obtain the effect of refining crystal grains. From this result, it is understood that the forging condition in which the crystal grain size is reduced to 10 μm or less in the superplastic forging of the crystal grain is, and the AZ61 to AZ3] alloy is in the range of Ζ値109-1013, preferably 101Q-1013. The scope. By using the above forging, the sample obtained by refining the crystal grains and the sample which is not refined are cut into a plate shape of 20 mm X 2 0 mm X 1.5 mm thick, and the sample is inserted into a die of a forging mold 20 mm. In the x 20 mm empty mold, Table 5 is unconditional to true strain -1. 1, forging in the shape of a casting with a cylindrical recess of 3 mm in diameter and 10 mm in height, forging forging Whether the sex is good is not in Table 5. According to the combination of 5 on the occasion - 22 - 1263681 into the '_ Huan ^ 0 § stretched Ra^ OsJ 1 1 1 500 3.3x10'2 4.4χ107 〇X 〇〇〇〇< 〇 〇〇400 3.3x10'2 9·9χ108 〇X 〇〇〇〇X 〇〇<] 350 3.3x1 Ο·2 6.9χ109 〇X 〇〇< 〇X 〇〇X ill gg 槪300 3.3x10'2 6.7 Χ1010 <] X 〇〇< 〇X 〇〇X 200 3.3x10'2 2·7χ1013 X <<<> 〇X 〇〇X 150 3.3x10'2 1·5χ1015 XXXXXXXXXX Forging temperature (°C) Ο C/D mm 粼m Ν Γ Γ Γ CNJ 00 Γ CO 卜 Γ Γ ο Τ Τ - Γ Γ Γ *τ— (£> 12.9 ο 18.8 ο Τ - CD inch · 14.2 Forging conditions ΑΖ81 ΑΖ51 ΑΖ41 ΑΖ31 ^ ^i§nDni ^ is—1^ πππ^^ιι^^^ιό s^i-Γ -23- (18) 1263681 The following facts can be recognized from Table 5. The grain boundary/3 phase is easy to precipitate, and it is easy to hinder the crystal. The composition of the aluminum with a large amount of sliding material must be formed at a higher processing temperature, that is, with a larger Z 。. On the other hand, even if the crystal grain size exceeds 1 〇 μ m, the alloy is processed in a relatively large manner. temperature Casting products can also be formed. However, if the mold temperature in the industry reaches above 40 °C, the durability of the mold is not practical. Although the use of heat-resistant materials or surface treatment can improve the high-temperature durability of the mold, It is not preferable that the cost of the mold is increased. From the results, it is understood that the alloy of AZ61 to AZ31 is in the range of Z 値 1013 or less, and is preferably in the range of 1 〇 8 - 1 〇 13 for the forging condition to be formed into a desired shape. Example 2 (1) Casting and Solution Treatment The casting test was carried out by die casting instead of the thixotropic die casting method of Example 1. The mold of the same shape of the molded article was formed by the use of the thixotropic die casting method, and the alloy was directly used for the touch. The alloy ingot of the same feed used in the variable-die casting machine is not first made into a wafer. The DC650 tCLS cold chamber die-casting machine made by Toshiba Machine Co., Ltd. is used to set the casting temperature 70 (TC, the injection speed at high speed). The casting was carried out in the order of 5.0 m/sec and the casting temperature was 25 Torr. The size and shape of each of the cast products were the same as in the first embodiment. The thixo-die casting method cannot be formed. The material can be cast by die-casting. This is because the die-casting method does not melt the material in the barrel of the molding machine like a thixotropic die-casting machine. Separately set in the liquid supply device -24- (19) 1263681 to melt the material, so the melting temperature can be as high as 70 (TC, and the melting point of AZ2 1 can also be melted. Each casting system and Example 1 The crystal grain size before and after the solution treatment was measured in the same manner, and the results are shown in Tables 6 and 3. Further, the solution treatment was carried out at 430 ° C for 1 hour. Table 6 Crystal grain size of the die-cast casting Alloy crystal grain size (μ m ) After solution treatment before solution treatment ΑΖ9 1 7.3 14.9 ΑΖ8 1 6.4 13.1 ΑΖ7 1 7.0 13.8 ΑΖ6 1 7.8 15.2 ΑΖ5 1 6.9 10.4 ΑΖ4 1 6.1 11.3 ΑΖ3 1 5.7 9.5 ΑΖ2 1 5.8 9.7
由表6及第3圖可知，壓鑄鑄造品之結晶粒徑較觸變模 鑄鑄造品之結晶粒徑爲小，即使不經結晶粒微細化之鍛造 處理，在溶體化處理前已小於1 〇 μπι。推論此係因成形機 之充塡速度快而有急冷效果之故。 (2 )鍛造 -25- (20) 1263681 所得之鑄造品由於結晶粒 之鍛造容易，以與實施例1中f 微細化之鍛造相同之條件進行 痕之鍛造。對溶體化處理前之 於晶界析出之相甚厚，不易 痕。此種傾向以鋁含量多者更 理後之樣品進行試驗。結果示 鑄鑄造品切割20mm X 20mm X 品以一定之應變速度成形。鍛 既已微細，因此爲使鑄造品 歸變模鑄之鑄造品之結晶粒 锻造，試驗是否可進行無裂 樣品進行預備鍛造試驗則因 產生晶界滑動，而易產生裂 爲顯著。因此僅以溶體化處 於表7。此時之樣品係自壓 1 , 5 m m厚之板狀，並將該樣 造之真應變爲-1 . 1。 -26- (21)1263681As can be seen from Tables 6 and 3, the crystal grain size of the die-cast casting product is smaller than that of the thixotropic die-casting product, and the forging treatment without the crystal grain refinement is less than 1 before the solution treatment. 〇μπι. It is inferred that this is due to the rapid filling effect of the forming machine and the quenching effect. (2) Forging -25- (20) 1263681 The obtained cast product was forged by the same conditions as in the forging of the microfine refining in Example 1, because the forging of the crystal grains was easy. The phase precipitated at the grain boundary before the solution treatment is very thick and is not easily traced. This tendency is tested with samples with more aluminum content. The result shows that the cast casting cut 20mm X 20mm X is formed at a certain strain rate. Since the forging is fine, the crystal grain forging of the cast product of the cast product of the cast product is forged, and whether the test can be carried out without cracking the sample for the preliminary forging test is caused by grain boundary sliding, which is liable to cause cracking. Therefore, only the solution was in Table 7. The sample at this time is self-pressed with a plate shape of 1 , 5 m m thick, and the true strain of the sample is -1. -26- (21)1263681
-27- (22) 1263681 由表7可認知下列事實。 亦即，與溶體化處理前之樣品同樣，若鋁含量多則有 鍛造性惡劣之傾向，於應變速度3.3 X 之條件下 ，AZ 9 1至AZ 7 1即使將加工溫度提高至3 5 0 °C以上，進行鍛 造時亦會產生缺陷。但若鋁含量減低則锻造變佳’雖然 AZ 9 1在任何溫度下其鍛造品均會產生破損，但AZ 8 1在3 0 0 °C以上（：亦即Z値小於6.7xl01() ) ，AZ71在250 °C以上（亦 即Z値小於1 . 0 X 1 0 1 2 )則不會產生裂痕，但產生小破損。 此外，若鋁含量減低則可鍛造而不會產生缺陷’ AZ6 1、AZ5 1 及 AZ4 1 在 2 5 0 °C 以上（亦即 Z 値小於 1 . 〇x 1 〇 12 )，AZ3 1與AZ2 1在200 °C以上（亦即Z値小於l.OxlO13) 則鍛造品不會產生缺陷而呈現優良之鍛造成形性。 由上述結果可謂將結晶粒徑繪造成爲1 〇 km以下之壓 鑄鑄造品之鍛造適宜組成爲鋁含量2-6質量％，而適宜之鍛 造條件爲Z値小於l.OxlO13者。 〔發明之效果〕 如上述，依據本發明之鎂合金之成形方法，於可鑄造 且鍛造性優越之鎂合金組成中，藉由組合鑄造與锻造使鎂 合金成形，而能以高良率製造具有複雜而精密之形狀，且 物性之可信度高，耐鈾性亦充分足夠之製品。 【圖式簡單說明】 第1圖係示實施例1之觸變模鑄鑄造品（溶體化處理後 -28 - (23) 1263681 )之結晶粒徑圖示。 第2圖係示實施例1之溶體化處理品於3 0 0 °C，ε ’= 1 . 0 χ 1 Ο _ 2 s e c_ 1之拉伸試驗結果。 第3圖係示實施例2之壓鑄鑄造品（溶體化處理後）之 結晶粒徑圖示。-27- (22) 1263681 The following facts can be recognized from Table 7. That is, as in the case of the sample before the solution treatment, if the aluminum content is large, the forgeability tends to be bad. Under the condition of a strain rate of 3.3 X, the AZ 9 1 to AZ 7 1 can increase the processing temperature to 3,500. Above °C, defects are also generated when forging. However, if the aluminum content is reduced, the forging becomes better. Although the AZ 9 1 will be damaged at any temperature, the AZ 8 1 is above 300 °C (ie, Z値 is less than 6.7xl01()). AZ71 above 250 °C (that is, Z 値 is less than 1.0 X 1 0 1 2) will not crack, but a small breakage. In addition, if the aluminum content is reduced, it can be forged without defects. AZ6 1, AZ5 1 and AZ4 1 are above 250 °C (that is, Z 値 is less than 1. 〇x 1 〇12 ), AZ3 1 and AZ2 1 Above 200 ° C (that is, Z 値 is less than 1.0 xxl13), the forged product does not cause defects and exhibits excellent forging properties. From the above results, it can be said that the forging composition of the die-casting product having a crystal grain size of 1 〇 km or less is an aluminum content of 2 to 6% by mass, and a suitable forging condition is Z 値 less than 1.00. [Effects of the Invention] As described above, according to the method for forming a magnesium alloy of the present invention, in a magnesium alloy composition which is excellent in castability and forgeability, a magnesium alloy is formed by combination casting and forging, and it can be manufactured with high yield. And the shape of precision, and the reliability of physical properties is high, and the uranium resistance is sufficient. BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a graph showing the crystal grain size of the thixotropic molded casting of Example 1 (after the solution treatment -28 - (23) 1263681). Fig. 2 is a graph showing the tensile test results of the solution treated product of Example 1 at 300 ° C, ε ' = 1.0 χ 1 Ο _ 2 s e c_1. Fig. 3 is a graph showing the crystal grain size of the die-cast product (after the solution treatment) of Example 2.
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