200916236 九、發明說明 【發明所屬之技術領域】 本發明是關於粉末壓縮成型製作成型體用的成型裝置 ’更詳細地說是關於N d - F e _ B系永久磁鐵等稀土永久磁鐵 製造時使用的成型裝置。 【先前技術】 稀土永久磁鐵，特別是Nd-Fe-B系燒結磁鐵（所謂钕 磁鐵），因是由鐵和價格便宜又資源豐富可穩定供應的 N d、B元素組合形成所以能夠以便宜價格製造的同時，又 因具有高磁性特性（最大能積爲鐵氧體磁鐵的1 0倍程度 )，所以被利用在電子機器等各種製品，近年來，也逐漸 成爲油電混合型車用的馬達或發電機所要採用的對象。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a molding apparatus for producing a molded body by powder compression molding, and more particularly to the production of a rare earth permanent magnet such as a N d - F e _ B permanent magnet. Molding device. [Prior Art] Rare earth permanent magnets, especially Nd-Fe-B based sintered magnets (so-called neodymium magnets), can be formed at a low price because they are formed by a combination of N and B elements which are inexpensive and resource-rich and can be stably supplied. At the same time, it is used in various products such as electronic equipment because it has high magnetic properties (maximum energy product is 10 times that of ferrite magnets). In recent years, it has gradually become a motor for hybrid electric vehicles. Or the object to be used by the generator.
Nd-Fe-B系燒結磁鐵的製造方法一例已知有粉末冶金 法’該方法，首先是將Nd、Fe、B以指定組成比加以混 合’經熔解、鑄造製成合金原料，利用例如氫粉碎作業步 驟使合金原料一旦粗粉碎後，接著，利用例如射流粉碎機 微粉碎作業步驟加以微粉碎，就可獲得合金原料粉末。其 次，將所獲得的合金原料粉末於磁場中加以定向（磁場定 向），接著在外加有磁場的狀態進行壓縮成型就可獲得成 型體。然後’將該成型體在指定條件下進行燒結就可製成 燒結磁鐵。 磁場中的壓縮成型法’一般是採用單軸加壓式的壓縮 成型機’該壓縮成型機是構成爲在模具貫通孔的模槽塡充 -4- 200916236 合金原料粉末’由一對衝頭從上下方向加壓（壓製）對合 金原料粉末進行壓縮成型，但由一對衝頭進行壓縮成型時 ’塡充在模槽內的合金原料粉末的粒子間的磨擦或合金原 料粉末和配設在衝頭的模具壁面的磨擦導致無法獲得高定 位性’無法達到提昇磁性特性的目的。因此，已知提案有 一種具有振動機構可在模槽塡充有合金原料粉後，於磁場 定向時使上衝頭及下衝頭當中至少一方朝加壓方向（壓製 方向）振動的壓縮成型裝置（例如專利文獻1 )。 〔專利文獻1〕國際公開2〇〇2/60677號公報（例如參 照申請專利範圍的記載） 【發明內容】 〔發明欲解決之課題〕 該壓縮成型裝置是構成爲只於磁場定向時使上衝頭及 下衝頭的任一方振動而已，所以在模槽內的合金原料粉末 粒子彼此的位置關係，於塡充在模槽內之後狀態幾乎沒有 改變。因此’當磁場定向方向爲相鄰的合金原料粉末粒子 彼此的結晶斷裂面（N d _ F e - B系燒結磁鐵的合金原料粉末 ，因是N d、F e、B進行混合，經熔解、合金化後加以粉 碎製成，所以於該合金原料粉末的表面’會形成有結晶斷 裂面）不吻合時’結果’間隙還是會殘留在合金原料粉末 的粒子間，導致合金原料粉末的容易磁化軸於磁場定向方 向形成不整齊’若在該狀態下進行壓縮成型則定向混亂， 以致產生無法獲得高定向性成型體的問題。 -5- 200916236 於是，有鑑於上述問題點，本發明的目的是在於提供 一種構成爲可在磁場中使較具有相等結晶取向關係的合金 原料粉末結晶斷裂面形成組合，藉此就能夠成型具有極高 定向性之成型體的成型裝置。 〔用以解決課題之手段〕 爲解決上述課題，申請專利範圍第1項記載的成型裝 置，其特徵爲，具備：磁場或電場中成極化的粉末塡充用 的塡充室；可對塡充在該塡充室內的粉末外加磁場或電場 的磁場或電場產生手段4 ;可在經由磁場或電場產生手段 外加有磁場或電場的狀態下對粉末進行攪拌加以定向的攪 拌手段；及可對被攪拌成定向的粉末於磁場或電場中施加 壓縮力使其成型的加壓手段。 根據本發明時，可使塡充於塡充室的粉末在磁場或電 場中經由攪拌手段對粉末進行攪拌加以定向，因此塡充室 內的粉末粒子彼此的位置關係是會產生變化形成不同於剛 境充在填充室內時的狀態’因此從fe場或電場定向方向的 結晶斷裂面之組合當中使較具有相等結晶取向關係的，結晶 斷裂面形成組合的機會就變多，具有相等結晶取向關係的 結晶斷裂面一旦結合，就會形成牢固的結合鏈，能爽j獲得 結晶斷裂面於fe;場定丨r!方向晕無間隙地整齊結合，目有高 定向性的定向體。接著，利用加壓手段，可在具有彳目等g 晶取向關係的結晶斷裂面彼此結合的狀態進行粉,縮$ 型，因此能夠獲得具有高定向性的成型體，同日寺胃w彳目胃 -6- 200916236 結晶取向關係的結晶斷裂面彼此是牢固結合著’因此以較 低的成型壓力就能夠獲得高密度的成型體。其結果，使成 型體的強度變強能夠降低瑕疵產生率。 上述攪拌手段最好是設置成可自由進退於塡充室內， 如此一來就能夠提昇對粉末進行成型壓縮藉此獲得成型體 時的作業性。 上述塡充室，具有將上述粉末塡充至該塡充室內時用 的開口，只要於上述攪拌手段一體設有當上述攪拌手段移 動至塡充室內時可封閉該開口的蓋體，就能夠防止粉末於 攪拌中飛出塡充室外側。 上述攪拌手段若是由非磁性材料構成時，則例如在磁 場中進行永久磁鐵用的合金原料粉末攪拌時，就能夠避免 合金原料粉末附著在攪拌手段，防止合金原料粉末攪拌不 足造成磁場混亂。 上述磁場產生手段，最好是能夠產生磁場強度爲5〜 3 0 k〇e範圍的靜磁場爲佳。於製作稀土永久磁鐵時，若磁 場強度比5 k 0 e還弱則無法獲得高定向性並且高磁性特性 的稀土永久磁鐵。另一方面’若磁場強度比3 〇 k 0 e還強 則磁場產生裝置會太大型’此外，裝置的耐久性會降低， 不付合實際需求。 另一方面，上述磁場產生手段，也可以是能夠產生5 〜5 0 k 0 e範圍的脈動脈衝磁場。如此一來，就能夠對塡充 在塡充室內的粉末本身施加振動，能夠更進一步提昇定向 性。不過’若磁場的強度比5〇 k0e還弱則無法獲得高定 200916236 向性並且高磁性特性的稀土永久磁鐵。另一方面，若磁場 強度比5 0 k 0 e is強則fe場產生裝置會太大型，此外，裝 置的耐久性會降低，不符合實際需求。 另，上述粉末，例如是以淬火法製成的稀土磁鐵用合 金原料粉末。如此一來，合金原料粉末是成爲銳角粒形狀 ’可使一個結晶斷裂面的面積較大，使合金原料粉末粒子 間的間隙變小，能夠提昇合金原料粉末的流動性再加上與 可使較具有相等結晶定向關係的合金原料粉末結晶斷裂面 形成組合的機會變多條件的相輔相成就能夠更進一步提高 定向性。其結果，採用本發明的成型裝置時，能夠獲得定 向不混亂且高密度又高磁性特性的永久磁鐵。 〔發明效果〕 如以上的說明，本發明的成型裝置，其發明效果爲， 可在磁場中使較具有相等結晶取向關係的合金原料粉末結 晶斷裂面形成組合，藉此就能夠製作出具極高定向性的成 型體。 【實施方式】 〔發明之最佳實施形態〕 參照第1圖至第5圖進行說明時，圖號1是表示本發 明的成型裝置，成型裝置1是應用在稀土永久磁鐵的製作 ’特別是應用在N d - F e - B系燒結磁鐵（定向體、成型體） 的製作。成型裝置1是加壓方向（壓製方向）垂直於磁場 -8 * 200916236 定向方向的一軸加壓式壓縮成型機，具有由腳板11支撐 的底座板1 2。於底座板1 2的上方配置著模具2，模具2 是由貫通在底座板12的複數支的支柱13所支撐著，各支 柱1 3的另一端是連結於底座板1 2下方所設置的連結板 1 4。連結板1 4是連接於驅動手段例如習知構造油壓缸筒 的油壓桿1 5，如此一來’當啓動下部油壓缸筒使連結板 14昇降時，就可使模具2朝上下方向（加壓方向γ)移 動自如。 於模具2的大致中央部形成有上下方向的貫通孔2 } ’於貫通孔21’從其下側可插入朝著上方豎立設置在底 座板12上面大致中央部的下衝頭31，當啓動下部油壓缸 筒使模具2下降時’下衝頭31會插入在貫通孔21內使貫 通孔2 1內區隔形成模槽（塡充室）2 2。習知構造的給粉 裝置（未圖示）是可對模槽22成自由進退於該給粉裝置 將事先枰好重量的下述合金原料粉末塡充至模槽22內。 於模具2上方配置有和底座板1 2成相向的模具底座 16。模具底座16的下面，在可插入模槽22的位置設有上 衝頭32，由上下一對的上衝頭32及下衝頭31構成加壓 手段。此外’模具底座1 6的角隅部形成有上下方向的貫 通孔’於各貫通孔插通著一端固定在模具2上面的導桿 1 7。此外’在模具底座1 6的上面連接有驅動手段例如習 知構造油壓缸筒（未圖示）的油壓桿1 8，當啓動該油壓 缸筒時’經由導桿1 7的引導，模具底座1 6會昇降自如， 連帶使上衝頭3 2朝上下方向（加壓方向）移動自如，能 -9- 200916236 夠插入在朝上下方向移動自如的模具2的貫通孔2 1內。 如此一來’於壓縮成型時，在模槽22內，由上下一對的 衝頭3 1、3 2對合金原料粉末p施加壓縮力進行成型，就 可獲指定形狀的成型體（成型步驟）。 此外’於模具2的外圍設有可使模槽22內的合金原 料粉末P磁場定向的磁場產生裝置4。磁場產生裝置4具 有從兩側夾著模具2成對稱配置，由軟鋼、純鐵或珀明德 鐵鈷類等導磁率高的材料製成的—對磁轭4 1 a、4 1 b。於 兩磁軛41a、41b捲繞有線圏42a、42b，對各線圈42a、 42b進行通電’藉此於加壓方向（上下方向γ)的正交方 向X產生靜磁場，如此一來，就能夠使塡充在模槽2 2內 的合金原料粉末P定向。 磁場中成極化的粉末即合金原料粉末p是經由下述作 業製成。即是將N d、F e、B以指定組成比加以混合，利 用淬火法例如脫模鑄造法先製成〇 · 0 5 m m〜0.5 m m的合金 。另一方面’也可利用離心鑄造法製成5mm程度厚的合 金’也可於混合時添加少量的Cu、Zr、Dy、A1或Ga。宜 次’將製成的合金利用習知氫粉碎作業使合金粗粉碎後， 接著’利用射流微碎機微粉碎作業在氮氣環境氣中進行微 粉碎，就可獲得平均粒徑爲2〜1 0 v m的合金原料粉末。 該狀況若採用淬火法，則合金原料粉末P會成爲銳角粒狀 ，可使一個結晶斷裂面的面積變大，可使合金原料粉末p 彼此間的間隙變小。 對於經由上述作業製成的合金原料粉末p ,爲讓：^流 -10- 200916236 動性提昇’最好是以指定混合比率添加潤滑劑，使合金原 料粉末p的表面披覆著該潤滑劑。潤滑劑是使用黏性低的 固體潤滑劑或液體潤滑劑以避免傷及模具。固體潤滑劑， 例如：層狀化合物（M〇S2、WS2、MoSe石墨BN、CFx等 )、軟質金屬（Zn、Pb等）、硬質物質（金剛石粉末、 TiN粉末等）、有機高分子（PTEE類、尼龍類脂肪族系 、高級脂肪族系、脂肪酸醯胺、脂肪酸酯類、金屬皂等） ，特別是以採用硬脂酸鋅、乙烯醯胺、氟代乙醚類潤滑劑 爲佳。 另一方面，液體潤滑劑，例如：天然油材料（蓖麻油 、椰子油、棕櫚油等植物油、礦油、石油類油脂）、有機 低分子材料（低級脂肪族系、低級脂肪酸醯胺類、低級脂 肪酸酯類）’特別是以採用液狀脂肪酸、液狀脂肪酸酯、 液狀氟素潤滑劑爲佳。液體潤滑劑，最好是和界面活性劑 一起使用較佳，或最好是以溶媒稀釋後使用較佳，由於燒 結後殘留的潤滑劑殘留碳成份會造成磁鐵的保磁力降低， 因此是以採用燒結作業容易去除的低分子量液體潤滑劑爲 佳。 對合金原料粉末P添加固體潤滑劑時，只要以 0· 02 wt%混合比率進行添加即可。若混合比率小於 0.02 wt%，則無法提昇合金原料粉末P的流動性，結果是 無法提昇定向性。另一方面，若混合比率超過0.02wt%， 則所獲得的燒結磁鐵會受到該燒結磁鐵中殘留的碳影響以 致保磁力降低。此外’對合金原料粉末P添加液體潤滑劑 -11 - 200916236 時，只要以0.05 wt%〜5 wt%範圍的比率進行添加即可。若 比率小於0 · 0 5 wt%，則無法提昇合金原料粉末p的流動性 ，結果是無法提昇定向性。另一方面，若混合比率超過 5 wt%，則所獲得的燒結磁鐵會受到該燒結磁鐵中殘留的 碳影響以致保磁力降低。另’潤滑劑的添加，若是採用固 體潤滑劑和液體潤滑劑雙方時，則潤滑劑會遍及合金原料 粉末P各個角落’能夠達到更高的潤滑效果，因此能夠獲 得更高的定向性。 將經由以上所述製成的合金原料粉末P塡充至形成在 模具2貫通孔21的模槽2 2後，雖然是由上下一對衝頭 31、32從上下方向加壓使合金原料粉末p壓縮成型，但 此時’爲了獲得局疋向性’需要謀求磁性特性的提昇。於 是，本實施形態是設有可對模槽2 2成自由進退的攪拌裝 置5。接著’將成型裝置1構成爲將合金原料粉末p塡充 至塡充室及模槽22後，在上下一對衝頭31、32進行壓縮 成型（成型步驟）之前’對磁場產生裝置4的各線圏42a 、4 2 b進行通電以成爲靜磁場產生狀態（磁場中），就能 夠一邊攪拌模槽2 2內的合金原料粉末p 一邊加以磁場定 向（定向步驟）。 攪拌裝置5具有平行設置在模具2上面的支撐板51 ，於支撐板5 1的上面，設有具習知構造的液壓缸筒5 2。 於突出在支撐板5 1下側的液壓缸筒52的液壓桿52a安裝 有習知構造的空氣驅動式馬達5 3，在配置成位於液壓桿 5 2 a長度方向軸線上的馬達5 3的旋轉軸5 3 a，安裝有旋轉 -12- 200916236 葉片54 (旋轉攪拌），由旋轉軸53a及旋轉葉片54構成 攪拌手段。旋轉葉片5 4是螺旋翼（螺旋槳）型，旋轉軸 53a及旋轉葉片54是非磁性材料製，例如是1 8-8不銹鋼 製。由於旋轉軸53a及旋轉葉片54是非磁性材料製，因 此於磁場中攪拌合金原料粉末時，就能夠避免合金原料粉 末P附著在攪拌手段，防止合金原料粉末P攪拌不足造成 磁場混亂。 支撐板51是安裝在朝著和上下方向成直角方向延伸 的2支導軌5 5，藉由沿著導軌5 5滑動支撐板5 1，使攪拌 裝置5對模槽22成自由進退。於該狀況，給粉裝置也可 安裝在同一導軌55藉此對模槽22成自由進退。接著，當 由設置在導軌5 5的止動器（未圖示）停止攪拌裝置5的 滑動時’旋轉軸5 3 a就會被定位在位於上下一對衝頭3 i 、3 2的長度方向軸線上。此外，於馬達5 3的旋轉軸5 3 a ，設有非磁性材料製的蓋板5 6，該蓋體5 6是在缸筒5 2 啓動使旋轉葉片54下降至模槽22內的指定位置上時，抵 接於模具2的上面以堵塞貫通孔2丨的上方，藉此達到防 止合金原料粉末P攪拌中飛出模槽22外側的效果。 如此一來’在對合金原料粉末P進行磁場定向時，就 可使藉由潤滑劑添加在合金原料粉末P以提昇合金原料粉 末流動性的措施’和藉由一邊外加磁場--邊對塡充在模槽 22內的合金原料粉末p進行攪拌以改變模槽22內合金原 料粉末P粒子彼此位置關係不同於剛塡充在模槽2 2內時 的狀態之措施相輔相成，使較具有相等結晶定向關係的合 -13- 200916236 金原料粉末結晶斷裂面形成組合的機會變多，具有相等結 晶取向關係的結晶斷裂面一旦結合，就會形成牢固的結合 鏈’能夠使結晶斷裂面於磁場定向方向毫無間隙結合成整 齊。以該狀態進行壓縮成型，就可成爲定向不混亂的高密 度成型體Μ (參照第5圖），能夠使成型體的強度變強降 低瑕疵產生率的同時，還能夠獲得高磁性特性的成型體Μ (永久磁鐵）。該狀況下’若是對塡充在模槽22內的合 金原料粉末Ρ事先混合樹脂黏合劑時，就可獲得高磁性特 性的稀土燒結磁鐵（成型體）。 其次’參照第1圖至第5圖’對使用本發明成型裝置 製造N d - F e - Β系燒結磁鐵時的製造過程進行說明。首先， 從模具2及下衝頭3 1的各上面爲同一平面，上衝頭3 2爲 位於上端的待機位置（參照第丨圖），啓動液壓缸筒使模 具2上昇至指定位置’在貫通孔2 1內區隔形成模槽2 2。 其次是由未圖示的給粉裝置’將事先秤好重量，以指定混 合比率添加有潤滑劑的合金原料粉末ρ塡充在模槽22內 ’接著使給粉裝置退出模槽22。於該狀況，爲了防止合 金原料粉末P偏移及保留攪拌時的自由度，模槽2 2內的 合金原料粉末P的塡充密度是設定成2.2〜3.9g/cc (參照 第2圖）。 其次，對攪拌裝置5進行移動，使馬達53的旋轉軸 5 3 &位於上下—對衝頭3 1、3 2的長度方向軸線上（參照 弟2圖）。接著’透過液壓缸筒5 2使馬達5 3及蓋板5 6 下降’讓蓋體56面接觸於模具2上面以堵塞貫通孔21上 -14- 200916236 面的同時，使旋轉葉片54埋設在模槽22內所塡充的合金 原料粉末P內（參照第3圖）。於該狀態，對磁場產生裝 置4的線圏42a、42b進行通電，在磁場中啓動馬達53使 旋轉葉片54旋轉在模槽22內（定向步驟）。該狀態下， 爲了獲得高定向性是在5k0e〜30k0e範圍的靜磁場中，更 好是在l〇kOe〜26k0e範圍的靜磁場中進行攪拌裝置5的 攪拌爲佳。磁場的強度若比5 k 0 e還弱，或比3 0 k 0 e還強 ’都無法獲得高定向性並且高磁性特性的成型體。此外， 爲讓塡充在模槽22內的合金原料粉末P整體攪拌混合， 旋轉葉片54的旋轉數爲！〇()〜50000 rpm，最好是設定成 4 0 00rpm ’只以指定時間（1〜5秒間）進行攪拌動作。 基於上述，如習知方法所示，例如即使利用上衝頭或 下衝頭施加振動，但如第4 ( a )圖所示在磁場定向方向 相鄰的合金原料粉末P彼此的結晶斷裂面不吻合時，間隙 會殘留在合金原料粉末P彼此之間，使合金原料粉末P於 磁場定向方向不整齊，以該狀態進行壓縮成型時定向會混 亂。相對於此，如本實施形態所示，只要在外加有磁場的 狀態下攪拌合金原料粉末P加以定向，就能夠使模槽22 內合金原料粉末P粒子彼此位置關係改變成不同於剛塡充 在模槽22內時的狀態，使較具有相等結晶取向關係的結 晶斷裂面形成組合的機會就變多，具有相等結晶取向關係 的結晶斷裂面一旦結合，就會形成牢固的結合鏈，如第4 (b )圖所示’可使結晶斷裂面剛好有如棒狀在磁場定向 方向毫無間隙結合成磁場定向方向整齊。 -15- 200916236 其次，磁場中的合金原料粉末p攪拌一旦結束， 昇液壓桿52 a使旋轉葉片5 4位於離開模具2上方的 後，沿著導軌5 5滑動退出攪拌裝置5。該狀況下， 有停止線圈4 2 a、4 2 b的通電。接著，使模具底座1 6 ，從貫通孔21的上側將上衝頭3 2插入貫通孔2 1， 加有磁場的狀態下由一對衝頭3 1、3 2在模槽2 2內開 行合金原來粉末P的壓縮成型。 經過指定時間後停止對線圈42a、42b通電，在 態下進行最大壓力的壓縮成型。最後，使上衝頭3 2 地上昇慢慢地減壓結束壓縮成型就可成型有成型體Μ 型步驟）。如此一來，因是以合金原來粉末剛好有如 在磁場定向方向毫無間隙結合成磁場定向方向整齊的 進行壓縮成型，所以就能夠獲得定向不混亂的高密度 體Μ (永久磁鐵），同時還提昇其磁性特性。 成型步驟的成型壓力是以設定在0.1〜1 t/cm2的 爲佳，更好是設定在0.2〜0.7 t/cm2的範圍。低於 t/cm2的成型壓力會導致成型體強度不足，例如從成 縮機的模槽22抽出時成型體會破裂。另一方面，超 t/cm2的成型壓力會造成過多的高成形壓力施力Π在模丰1 內的合金原來粉末P，導致定向邊崩塌邊成型的同時 怕成型體還會產生龜裂或破損。此外，成型步驟的磁 強度是設定在5 kOe〜30 kOe的範圍。若磁場強度比f 還弱則無法獲得高定向性並且高磁性特性的成型體。 方面，若磁場強度比3 0 kOe還強則磁場產生裝置會 就上 位置 並沒 下降 在外 始進 該狀 慢慢 (成 棒狀 狀態 成型 範圍 0. 1 型壓 過1 | 22 ，恐 場的 ! k0 e 另一 太大 -16- 200916236 型不符合實際需求。 其次是在外加例如3 k 0 e的逆磁場進行退磁後 具2下降至下降端，就可使模槽22內的成型體Μ 模具2上面，接著上昇模具底座1 6使上衝頭3 2移 昇端後就可取出成型體。最後，將獲得的成型體收 圖示的燒結爐內，例如在Ar環境氣下以指定溫度 °C )進行指定時間燒結（燒結步驟），又以指定 5 0 0 °C )在Ar環境氣中進行指定時間時效處理就可 結磁鐵（Nd-Fe-B系永久磁鐵）。 本實施形態是針對成型方向垂直磁場方向的一 式的構成進行了說明，但並不限於此，也可採用成 和磁場方向平行的構成。此外，本實施形態，對於 成型時的定向磁場是採用每單位時間的磁場強度爲 靜磁場，但並不限於此，如第6圖所示，可採用每 間的磁場強度以一定週期變化的脈動脈衝磁場。於 ’如第7圖所示，也構成爲可外加有逆磁場。 如此一來’合金原料粉末P的攪拌及成型時就 合金原料粉末P施加振動。能夠更進一步提昇定向 該狀況’脈衝的週期是以1 ms〜2s爲佳，此外，非 間是以設定在5 0 0 m s以下爲佳。超過該範圍時會造 的結合鏈斷掉’無法獲得高定向性。另外，在外加 衝磁場時’以其峰値設定在5〜5 0 k 0 e的範圍爲佳 場強度比5 kOe還弱則無法獲得高定向性並且高磁 的成型體。另一方面’若磁場強度比5〇 kOe還強 ，將模 抽出在 動至上 納在未 (1000 溫度（ 獲得燒 軸加壓 型方向 攪拌及 不變的 單位時 該狀況 能夠對 性。於 輸出時 成牢固 脈動脈 。若磁 性特性 則磁場 -17- 200916236 產生裝置會太大型不符合實際需求。 此外’本實施形態是針對攪拌手段採用螺旋漿型旋轉 葉片5 4的構成進行了說明（旋轉攪拌），但並不限於此 ，攪拌手段也可構成爲於油壓缸筒52的油壓桿52a的前 端，安裝有已設有空氣缸筒等驅動手段的矩形攪拌片（未 圖示）’在該攪拌片埋設於合金原料粉末p的狀態下，以 指定週期水平往復動作成遍及模槽2 2半徑方向全長（水 平攪拌）。旋轉攪拌或水平攪拌時，也可使油壓桿52a上 下動作，使模槽22內的合金原料粉末p整體攪拌混合》 另外，對於旋轉攪拌方式所採用的旋轉葉片5 4，只 要是能夠於攪拌中使合金原料粉末P整體攪拌混合的構成 ’並無特別加以限定’也可採用產生氣流進行攪拌的構成 ，但其形狀還是以攪拌中難以造成合金原料粉末P粉碎的 形狀爲佳。如第8圖所示，旋轉葉片，例如可採用大致L 字型板片5 4 a以9 0度角度錯開設置在旋轉軸的槳輪葉片 型[參照第8 ( a )圖]，或採用葉片54b成旋轉狀設置的螺 條葉片型[參照第8 ( b )圖]，或採用具有板片54c延伸平 行於旋轉軸的錨式葉片型[參照第8 ( c )圖]，然後根據所 選擇的旋轉葉片種類對旋轉數及攪拌時間加以適宜設定。 另一方面，攪拌手段並不限於旋轉攪伴或水平攪拌’也可 於油壓桿5 2 a前端安裝有氣體噴嘴由非磁性材料構成攪拌 手段，以間歇性或連續噴射高壓氣體對模槽22內的合金 原料粉末P進行攪拌。 此外，本實施形態是針對使用單軸加壓式成型裝置1 -18- 200916236 進行粉末成型的構成進行了說明，但並不限於此，成型裝 置也可採用橡膠鑄模的靜水壓型構成（未圖示）。於該狀 況，將合金原料粉末P塡充在塡充室構成用的橡膠鑄模內 後，實施由攪拌裝置5在磁場中進行攪拌的定向步驟。另 一方面’也可將經由一軸加壓式成型裝置1成型步驟所獲 得的成型體Μ ’又使用靜水壓成型裝置進行再度成型實施 第二成型步驟。如此一來，就能夠降低成型體的龜裂或破 損。 另外’本實施形態是使用成型裝置1將合金原料粉末 Ρ在磁場中進行攪拌的同時加以磁場定向製成定向體，接 著，在外加有磁場的狀態下進行壓縮成型製作出成型體， 但例如也可將經由上述所獲得的合金原料粉末塡充在上面 形成開口的Mo製箱體，利用上述攪拌裝置5在磁場中進 行指定時間攪拌’退出攪拌裝置5後，不進行退磁，而是 將Mo製蓋體安裝在箱體的上面開口之後，減弱磁場，接 著’將安裝有蓋體的箱體直接放入燒結爐進行燒結製作永 久磁鐵（燒結體）。於該狀況’磁場的強度是設定成 I2k0e’箱體是形成爲7cm的立方體，攪拌裝置5的旋轉 數是設定成40000rpm，攪拌時間是設定成2秒，藉此獲 得的燒結體是 Br=15.01kG、（BH) max = 55.1MG0e，可獲 得定向度9 9 %的平均磁鐵特性。 再加上’本實施形態是以燒結磁鐵的製造爲例進行了 說明’但只要是可使磁場或電場中極化的粉未定向製作出 定向體’對該定向體進行壓縮成型的製造，就可採用本發 -19- 200916236 明的成型裝置1。例如：將指定的粉末在磁場中成型後進 fT燒結形成氮化砂（S i 3 N 4 )燒結體的製造。 【圖式簡單說明】 第1圖爲本發明製造方法實施用的成型裝置待機位置 狀態說明圖。 第2圖爲第1圖所示成型裝置的動作說明圖。 第3圖爲第1圖所示成型裝置的動作（定向步驟）說 明圖。 第4 ( a )圖爲習知技術的磁場定向說明圖，第4 ( b )圖爲本發明的攪拌磁場定向說明圖。 第5圖爲第1圖所示成型裝置的動作（成型步驟）說 明圖。 第6圖爲脈動脈衝磁場說明圖。 第7圖爲脈動脈衝磁場的變形例說明圖。 第8( a )圖至第8(c)圖爲表示攪拌裝置所使用的 旋轉葉片其他形態圖。 【主要元件符號說明】 1 :壓縮成型機 2 :模具 2 1 :貫通孔 22 :模槽 3 1、3 2 :衝頭 -20- 200916236 4 :磁場產生裝置 5 :攪伴裝置 54 :旋轉葉片 56 :蓋體 P :合金原料粉末An example of a method for producing a sintered Nd-Fe-B sintered magnet is a powder metallurgy method. First, Nd, Fe, and B are mixed at a specified composition ratio. The alloy raw material is melted and cast, and pulverized by, for example, hydrogen. In the working step, once the alloy raw material is coarsely pulverized, it is then finely pulverized by, for example, a jet mill fine pulverization operation step, whereby an alloy raw material powder can be obtained. Then, the obtained alloy raw material powder is oriented in a magnetic field (magnetic field orientation), and then compression-molded in a state in which a magnetic field is applied to obtain a molded body. Then, the molded body is sintered under specified conditions to form a sintered magnet. The compression molding method in the magnetic field is generally a uniaxial compression type compression molding machine. The compression molding machine is configured to mold the mold in the through hole of the mold - 200916236 alloy raw material powder 'from a pair of punches from top to bottom Directional pressurization (pressing) compression molding of the alloy raw material powder, but when the compression molding is performed by a pair of punches, the friction between the particles of the alloy raw material powder filled in the cavity or the alloy raw material powder and the powder disposed at the punch The friction of the mold wall surface results in the inability to obtain high positioning properties, which cannot achieve the purpose of improving magnetic properties. Therefore, it is known that there is a compression molding apparatus having a vibration mechanism capable of vibrating at least one of the upper punch and the lower punch in the pressing direction (pressing direction) when the magnetic field is oriented after the cavity is filled with the alloy raw material powder. (for example, Patent Document 1). [Patent Document 1] International Publication No. 2〇〇2/60677 (for example, refer to the description of the scope of the patent application) [Problem to be Solved by the Invention] The compression molding apparatus is configured to make an overshoot only when the magnetic field is oriented. Since either of the head and the lower punch vibrates, the positional relationship between the alloy raw material powder particles in the cavity is hardly changed after filling in the cavity. Therefore, 'when the direction of the magnetic field is the crystal fracture surface of the adjacent alloy raw material powder particles (the alloy raw material powder of the N d _ F e - B based sintered magnet, because N d, F e, B are mixed, melted, After alloying, it is pulverized. Therefore, when the surface of the alloy raw material powder is formed with a crystal fracture surface, the 'result' gap remains between the particles of the alloy raw material powder, resulting in an easy magnetization axis of the alloy raw material powder. If the compression direction is performed in this state, the orientation is disordered, so that the problem that the highly directional molded body cannot be obtained is caused. -5- 200916236 Thus, in view of the above problems, an object of the present invention is to provide a crystal fracture surface of an alloy raw material powder which is configured to have a relatively uniform crystal orientation relationship in a magnetic field, thereby being capable of forming a pole. A molding device for a highly oriented molded body. [Means for Solving the Problem] In the molding apparatus according to the first aspect of the invention, the molding apparatus according to the first aspect of the invention is characterized in that: the charging chamber for charging the magnetic field in the magnetic field or the electric field is provided; a magnetic field or an electric field generating means 4 for applying a magnetic field or an electric field to the powder in the charging chamber; a stirring means for orienting the powder in a state in which a magnetic field or an electric field is applied via a magnetic field or an electric field generating means; and the stirring means A pressurized means in which a directed powder is subjected to a compressive force in a magnetic or electric field to form it. According to the present invention, the powder which is filled in the charging chamber can be oriented by stirring the powder in a magnetic field or an electric field via a stirring means, so that the positional relationship between the powder particles in the charging chamber is changed to form a difference from the rigid environment. The state in which it is filled in the filling chamber. Therefore, from the combination of the crystal fracture surface in the direction of the field of the fe field or the direction of the electric field, the crystal fracture surface is more likely to form a combination with a crystal orientation, and the crystal has an equal crystal orientation relationship. Once the fracture surface is combined, a strong bond chain will be formed, and the crystal fracture surface can be obtained in the field; the field is fixed in the direction of r! and the gap is neatly combined without any gap, and the oriented body with high orientation is obtained. Then, by means of a pressurizing means, the crystal fracture surface having a g crystal orientation relationship such as an eye-catching relationship can be combined with each other in a state of being combined with each other. Therefore, a molded body having high orientation can be obtained, and the same stomach can be obtained. -6- 200916236 The crystal fracture surfaces of the crystal orientation relationship are firmly bonded to each other. Therefore, a high-density molded body can be obtained at a low molding pressure. As a result, the strength of the molded body is made stronger, and the rate of occurrence of ruthenium can be lowered. It is preferable that the agitation means is provided so as to be freely advanced and retractable in the refilling chamber, whereby the workability in obtaining the molded body by molding compression of the powder can be improved. The filling chamber has an opening for filling the powder into the charging chamber, and can be prevented by integrally providing the stirring means with a lid that can close the opening when the stirring means is moved into the charging chamber. The powder flies out of the mixing chamber while stirring. When the stirring means is made of a non-magnetic material, for example, when the alloy raw material powder for the permanent magnet is stirred in the magnetic field, it is possible to prevent the alloy raw material powder from adhering to the stirring means and prevent the alloy raw material powder from being stirred insufficiently to cause magnetic field disturbance. Preferably, the magnetic field generating means is capable of generating a static magnetic field having a magnetic field intensity of 5 to 30 k〇e. When a rare earth permanent magnet is produced, if the magnetic field intensity is weaker than 5 k 0 e, a rare earth permanent magnet having high directivity and high magnetic properties cannot be obtained. On the other hand, if the magnetic field strength is stronger than 3 〇 k 0 e, the magnetic field generating device will be too large. In addition, the durability of the device will be lowered, and the actual demand will not be met. On the other hand, the magnetic field generating means may be a pulsating pulse magnetic field capable of generating a range of 5 to 5 0 k 0 e. In this way, it is possible to apply vibration to the powder itself which is filled in the charging chamber, and the orientation can be further improved. However, if the intensity of the magnetic field is weaker than 5 〇 k0e, it is impossible to obtain a rare earth permanent magnet with a high magnetic property of 200916236. On the other hand, if the magnetic field strength is stronger than 50 k ei is, the fe field generating device will be too large, and the durability of the device will be lowered to meet the actual demand. Further, the above powder is, for example, an alloy raw material powder for a rare earth magnet produced by a quenching method. In this way, the alloy raw material powder has an acute-angled particle shape, which can make the area of one crystal fracture surface larger, thereby making the gap between the alloy raw material powder particles smaller, and improving the fluidity of the alloy raw material powder. The crystal fracture surface of the alloy raw material powder having an equal crystal orientation relationship forms a combination of chances of multi-conditional complementary phase achievement to further improve the orientation. As a result, when the molding apparatus of the present invention is used, it is possible to obtain a permanent magnet which is not disordered and has high density and high magnetic properties. [Effect of the Invention] As described above, the molding apparatus of the present invention has an effect of being able to form a crystal fracture surface of an alloy raw material powder having a uniform crystal orientation relationship in a magnetic field, whereby an extremely high orientation can be produced. Sexual molded body. [Embodiment] BEST MODE FOR CARRYING OUT THE INVENTION Referring to Figs. 1 to 5, Fig. 1 shows a molding apparatus of the present invention, and molding apparatus 1 is applied to the production of rare earth permanent magnets, particularly application. Production of N d - F e - B based sintered magnets (oriented bodies, molded bodies). The molding apparatus 1 is a one-shaft compression type compression molding machine in which the pressing direction (pressing direction) is perpendicular to the direction of the magnetic field -8 * 200916236, and has a base plate 12 supported by the leg plate 11. A mold 2 is disposed above the base plate 12, and the mold 2 is supported by a plurality of pillars 13 penetrating the base plate 12. The other end of each pillar 13 is connected to a joint provided below the base plate 12. Board 1 4. The connecting plate 14 is a hydraulic rod 15 connected to a driving means such as a conventionally constructed hydraulic cylinder, so that when the lower hydraulic cylinder is activated to raise and lower the connecting plate 14, the mold 2 can be moved up and down. (Pressure direction γ) moves freely. A through hole 2 is formed in a substantially central portion of the mold 2 in the vertical direction. The through hole 21' is insertable from the lower side thereof into a lower punch 31 which is erected upwardly at a substantially central portion of the upper surface of the base plate 12, when the lower portion is activated. When the hydraulic cylinder causes the mold 2 to descend, the lower punch 31 is inserted into the through hole 21 to form a cavity (filling chamber) 2 2 in the through hole 2 1 . The powder feeding device (not shown) of the conventional structure is capable of freely advancing and retreating the mold groove 22 to the powder feeding device, and the following alloy raw material powder which has been previously weighed is filled into the cavity 22. A mold base 16 facing the base plate 12 is disposed above the mold 2. On the lower surface of the mold base 16, an upper punch 32 is provided at a position where the cavity 22 can be inserted, and a pair of upper and lower punches 32 and a lower punch 31 constitute a pressurizing means. Further, the corner portion of the mold base 16 is formed with a through hole in the vertical direction, and a guide rod 17 having one end fixed to the upper surface of the mold 2 is inserted into each of the through holes. Further, a hydraulic lever 18 such as a conventionally constructed hydraulic cylinder (not shown) is connected to the upper surface of the mold base 16 and is guided by the guide rod 17 when the hydraulic cylinder is activated. The mold base 16 is lifted and lowered, and the upper punch 3 2 is moved freely in the up-and-down direction (pressing direction), and can be inserted into the through hole 2 1 of the mold 2 that can move freely in the up-and-down direction. In the case of the compression molding, a molding force of a predetermined shape is obtained by applying a compressive force to the alloy raw material powder p by the pair of upper and lower punches 3 1 and 3 2 in the cavity 22 (forming step). . Further, a magnetic field generating means 4 for orienting the magnetic field of the alloy raw material powder P in the cavity 22 is provided on the periphery of the mold 2. The magnetic field generating device 4 has a pair of yokes 4 1 a and 4 1 b made of a material having a high magnetic permeability such as mild steel, pure iron or Perminder iron cobalt, which are symmetrically arranged from both sides with the mold 2 interposed therebetween. The coils 42a and 42b are wound around the yokes 41a and 41b, and the coils 42a and 42b are energized to generate a static magnetic field in the orthogonal direction X of the pressurizing direction (the vertical direction γ), so that the magnetic field can be generated. The alloy raw material powder P which is filled in the cavity 2 2 is oriented. The powder which is polarized in the magnetic field, that is, the alloy raw material powder p, is produced by the following work. That is, N d , F e , and B are mixed at a specified composition ratio, and an alloy of 〇 · 0 5 m m to 0.5 m m is first formed by a quenching method such as mold release casting. On the other hand, it is also possible to form a gold alloy having a thickness of 5 mm by a centrifugal casting method. It is also possible to add a small amount of Cu, Zr, Dy, A1 or Ga at the time of mixing. Yiji's the alloy to be coarsely pulverized by a conventional hydrogen pulverization operation, and then finely pulverized in a nitrogen atmosphere by a micro-crushing operation of a jet micro-crusher to obtain an average particle diameter of 2 to 10 vm. Alloy raw material powder. In this case, when the quenching method is employed, the alloy raw material powder P becomes an acute-angled granular shape, and the area of one crystal fracture surface can be increased, and the gap between the alloy raw material powders p can be made small. For the alloy raw material powder p produced through the above operation, it is preferable to add a lubricant at a predetermined mixing ratio so that the surface of the alloy raw material powder p is coated with the lubricant. Lubricants use a low viscosity solid lubricant or liquid lubricant to avoid injury to the mold. Solid lubricants such as layered compounds (M〇S2, WS2, MoSe graphite BN, CFx, etc.), soft metals (Zn, Pb, etc.), hard substances (diamond powder, TiN powder, etc.), organic polymers (PTEE type) , nylon aliphatic, higher aliphatic, fatty acid decylamine, fatty acid esters, metal soap, etc.), especially using zinc stearate, vinyl amide, fluoroethyl ether lubricants. On the other hand, liquid lubricants such as natural oil materials (vegetable oil such as castor oil, coconut oil, palm oil, mineral oil, petroleum oils), organic low molecular materials (lower aliphatic, lower fatty acid guanamines, lower grades) The fatty acid esters are preferably selected from the group consisting of liquid fatty acids, liquid fatty acid esters, and liquid fluorocarbon lubricants. The liquid lubricant is preferably used together with a surfactant, or preferably diluted with a solvent, and the residual carbon residue of the residual lubricant after sintering causes a decrease in the coercive force of the magnet. A low molecular weight liquid lubricant which is easily removed by a sintering operation is preferred. When a solid lubricant is added to the alloy raw material powder P, it may be added at a mixing ratio of 0. 02 wt%. If the mixing ratio is less than 0.02 wt%, the fluidity of the alloy raw material powder P cannot be improved, and as a result, the orientation cannot be improved. On the other hand, if the mixing ratio exceeds 0.02% by weight, the obtained sintered magnet is affected by the residual carbon in the sintered magnet to lower the coercive force. Further, when the liquid lubricant -11 - 200916236 is added to the alloy raw material powder P, it may be added in a ratio ranging from 0.05 wt% to 5 wt%. If the ratio is less than 0 · 0 5 wt%, the fluidity of the alloy raw material powder p cannot be improved, and as a result, the orientation cannot be improved. On the other hand, if the mixing ratio exceeds 5 wt%, the obtained sintered magnet is affected by the residual carbon in the sintered magnet to lower the coercive force. In addition, when the lubricant is added, if both the solid lubricant and the liquid lubricant are used, the lubricant can reach a higher lubricating effect throughout the corners of the alloy raw material powder P, so that higher orientation can be obtained. After the alloy raw material powder P produced as described above is filled into the cavity 2 2 formed in the through hole 21 of the mold 2, the alloy raw material powder p is compressed by pressurization from the upper and lower sides by the upper and lower pair of punches 31 and 32. Molding, but at this time 'in order to obtain the bureaucraticity', it is necessary to improve the magnetic properties. Therefore, in the present embodiment, the stirring device 5 capable of freely advancing and retracting the cavity 22 is provided. Then, the molding apparatus 1 is configured to charge the alloy raw material powder p to the charging chamber and the cavity 22, and before the compression molding (forming step) of the upper and lower punches 31 and 32, the respective paths of the magnetic field generating device 4 When 42a and 4 2 b are energized to be in a static magnetic field generating state (in a magnetic field), the magnetic field orientation (orientation step) can be performed while stirring the alloy raw material powder p in the cavity 2 2 . The stirring device 5 has a support plate 51 which is disposed in parallel on the upper surface of the mold 2. On the upper surface of the support plate 51, a hydraulic cylinder 5 having a conventional structure is provided. The hydraulic rod 52a of the cylinder block 52 projecting from the lower side of the support plate 5 is mounted with a conventionally constructed air-driven motor 53 for rotation of the motor 53 disposed on the longitudinal axis of the hydraulic rod 52a. The shaft 5 3 a is attached with a rotary -12-200916236 blade 54 (rotary stirring), and the rotating shaft 53a and the rotating blade 54 constitute a stirring means. The rotary vane 54 is of a spiral type (propeller type), and the rotary shaft 53a and the rotary vane 54 are made of a non-magnetic material, for example, made of 18-8 stainless steel. Since the rotating shaft 53a and the rotary vane 54 are made of a non-magnetic material, the alloy raw material powder P can be prevented from adhering to the stirring means when the alloy raw material powder is stirred in the magnetic field, and the magnetic field disorder can be prevented from being insufficient due to insufficient stirring of the alloy raw material powder P. The support plate 51 is mounted on two guide rails 5 extending in a direction perpendicular to the up-and-down direction, and the agitating device 5 is freely advanced and retracted to the cavity 22 by sliding the support plate 5 1 along the guide rails 5. In this case, the powder feeding device can also be mounted on the same guide rail 55 to thereby advance and retreat to the cavity 22. Next, when the sliding of the stirring device 5 is stopped by a stopper (not shown) provided on the guide rail 5, the 'rotating shaft 53' is positioned at the longitudinal axis of the pair of upper and lower punches 3i, 3 2 on-line. Further, a cover plate 5 6 made of a non-magnetic material is provided on the rotating shaft 5 3 a of the motor 53, and the cover body 56 is activated at a specified position in the cylinder barrel 52 to lower the rotary vane 54 into the cavity 22. In the upper direction, the upper surface of the mold 2 is abutted to block the upper side of the through hole 2丨, thereby preventing the alloy raw material powder P from flying out of the cavity 22 during stirring. In this way, when the magnetic field orientation of the alloy raw material powder P is performed, the lubricant raw material powder P can be added to improve the fluidity of the alloy raw material powder, and the magnetic field can be added by one side. The alloy raw material powder p in the cavity 22 is agitated to change the positional relationship of the alloy raw material powder P particles in the cavity 22 to be different from the state when the crucible is filled in the cavity 2 2, so that the crystal orientation is equal. The relationship of the combination of -13-200916236 gold raw material powder crystal fracture surface forming a combination of opportunities, the crystal fracture surface with equal crystal orientation relationship, once combined, will form a strong bond chain 'can make the crystal fracture surface in the direction of the magnetic field orientation No gaps are combined into a neat. By performing compression molding in this state, it is possible to obtain a high-density molded body which is not disordered in orientation (see Fig. 5), and it is possible to obtain a molded body having high magnetic properties while increasing the strength of the molded body. Μ (permanent magnet). In this case, a rare earth sintered magnet (molded body) having high magnetic properties can be obtained by previously mixing a resin binder with the alloy raw material powder which is filled in the cavity 22. Next, the manufacturing process when the N d - F e - lanthanide sintered magnet is produced by using the molding apparatus of the present invention will be described with reference to Figs. 1 to 5 . First, the upper surface of each of the mold 2 and the lower punch 3 1 is the same plane, and the upper punch 32 is a standby position at the upper end (refer to the first drawing), and the hydraulic cylinder is started to raise the mold 2 to the designated position. The inner portion of the hole 2 1 is formed into a cavity 2 2 . Next, the powder feeding device (not shown) is weighed in advance, and the alloy raw material powder ρ which is added with the lubricant at the specified mixing ratio is filled in the cavity 22, and then the powder feeding device is withdrawn from the cavity 22. In this case, in order to prevent the offset of the alloy raw material powder P and the degree of freedom in stirring, the enthalpy density of the alloy raw material powder P in the cavity 2 2 is set to 2.2 to 3.9 g/cc (see Fig. 2). Next, the stirring device 5 is moved so that the rotating shafts 5 3 & of the motor 53 are located on the longitudinal axis of the upper and lower punches 3 1 and 3 2 (see Fig. 2). Then, 'the motor 5 3 and the cover plate 56 are lowered by the hydraulic cylinder 5', and the cover 56 is brought into surface contact with the upper surface of the mold 2 to block the surface of the through hole 21 from the -14 to 200916236, and the rotary vane 54 is buried in the mold. The inside of the alloy raw material powder P to be filled in the tank 22 (refer to Fig. 3). In this state, the turns 42a, 42b of the magnetic field generating means 4 are energized, and the motor 53 is activated in the magnetic field to rotate the rotary vane 54 in the cavity 22 (orientation step). In this state, in order to obtain high directivity, it is preferable to stir the stirring device 5 in a static magnetic field in the range of 5k0e to 30k0e, and more preferably in a static magnetic field in the range of l〇kOe to 26k0e. If the intensity of the magnetic field is weaker than 5 k 0 e or stronger than 30 k 0 e, it is impossible to obtain a molded body having high directivity and high magnetic properties. Further, in order to stir and mix the alloy raw material powder P which is filled in the cavity 22 as a whole, the number of rotations of the rotary vane 54 is! 〇()~50000 rpm, preferably set to 4 00 rpm ‘The stirring operation is performed only for a specified time (between 1 and 5 seconds). Based on the above, as shown in the conventional method, for example, even if vibration is applied by the upper punch or the lower punch, the crystal fracture surfaces of the alloy raw material powders P adjacent to each other in the direction of the magnetic field orientation as shown in Fig. 4(a) are not At the time of the coincidence, the gap remains between the alloy raw material powders P, so that the alloy raw material powder P is not aligned in the direction in which the magnetic field is oriented, and the orientation is confusing when compression molding is performed in this state. On the other hand, as shown in the present embodiment, if the alloy raw material powder P is stirred and oriented in a state where a magnetic field is applied, the positional relationship of the alloy raw material powder P particles in the cavity 22 can be changed to be different from that of the steel. In the state in the cavity 22, the chance of forming a combination of crystal fracture surfaces having an equal crystal orientation relationship is increased, and once the crystal fracture planes having the same crystal orientation relationship are combined, a strong bond chain is formed, such as the fourth. (b) As shown in the figure, 'the crystal fracture surface can be just as well as the rod shape in the direction of the magnetic field without any gap combined into a magnetic field orientation direction. -15- 200916236 Next, once the stirring of the alloy raw material powder p in the magnetic field is completed, the lifting hydraulic rod 52 a slides the rotating blade 5 4 out of the mold 2 and slides off the stirring device 5 along the guide rail 55. In this case, the energization of the coils 4 2 a, 4 2 b is stopped. Next, the mold base 16 is inserted into the through hole 2 from the upper side of the through hole 21, and the alloy is opened in the cavity 2 2 by a pair of punches 3 1 and 3 2 in a state where a magnetic field is applied. Original compression molding of powder P. After the specified time has elapsed, the energization of the coils 42a, 42b is stopped, and the maximum pressure compression molding is performed in the state. Finally, the upper punch 3 2 is raised and the pressure is gradually reduced to complete the compression molding to form a molded body 步骤 type step). In this way, since the original powder of the alloy is just like the compression molding in the direction in which the magnetic field is oriented without any gap and the direction of the magnetic field is aligned, it is possible to obtain a high-density body (permanent magnet) which is not disordered in orientation, and also improves Its magnetic properties. The molding pressure in the molding step is preferably set to 0.1 to 1 t/cm2, more preferably in the range of 0.2 to 0.7 t/cm2. A molding pressure lower than t/cm2 causes insufficient strength of the molded body, for example, the molded body is broken when it is taken out from the cavity 22 of the compressor. On the other hand, the molding pressure of super t/cm2 causes too much high forming pressure to apply the original powder P of the alloy in the mold 1 to cause the formation of the directional ablation and the formation of cracks or breakage of the molded body. . Further, the magnetic strength of the molding step is set in the range of 5 kOe to 30 kOe. If the magnetic field strength is weaker than f, a molded body having high directivity and high magnetic properties cannot be obtained. On the other hand, if the magnetic field strength is stronger than 30 kOe, the magnetic field generating device will not go down and start slowly in the upper position (in the shape of a rod, the molding range is 0. 1 type is over 1 | 22, fear field! K0 e Another too large -1616236 type does not meet the actual demand. Secondly, after adding a reverse magnetic field of, for example, 3 k 0 e for demagnetization, with 2 falling to the lower end, the molded body in the cavity 22 can be molded. 2 above, then the mold base 16 is raised, the upper punch 3 2 is moved to the end, and the molded body can be taken out. Finally, the obtained molded body is shown in the sintering furnace, for example, under the Ar ambient gas at a specified temperature. C) The magnet is sintered (Nd-Fe-B permanent magnet) by performing sintering at the specified time (sintering step) and aging at a specified time in Ar ambient gas at a specified time. In the present embodiment, the configuration of the vertical magnetic field direction in the molding direction has been described. However, the present invention is not limited thereto, and a configuration in which the direction of the magnetic field is parallel may be employed. Further, in the present embodiment, the magnetic field intensity per unit time is a static magnetic field for the orientation magnetic field at the time of molding, but the present invention is not limited thereto, and as shown in Fig. 6, the pulsation of the magnetic field intensity per unit period may be employed. Pulsed magnetic field. As shown in Fig. 7, it is also constructed such that a reverse magnetic field can be applied. As a result, vibration is applied to the alloy raw material powder P during the stirring and molding of the alloy raw material powder P. The orientation can be further improved. The period of the pulse is preferably 1 ms to 2 s, and the interval is preferably set to 500 s or less. When the ratio exceeds this range, the bond chain which is made is broken, and high orientation cannot be obtained. Further, when the external magnetic field is applied, the range of 5 to 5 0 k 0 e is set to be a good field strength of 5 kOe, and a highly directional and highly magnetic molded body cannot be obtained. On the other hand, if the magnetic field strength is stronger than 5〇kOe, the mold is extracted and moved to the upper stage (1000 temperature (this condition can be matched when the stirring axis is in the direction of constant pressure and constant unit is obtained. It is a strong vascular artery. If the magnetic properties are used, the magnetic field -17-200916236 will be too large to meet the actual needs. In addition, this embodiment describes the configuration in which the propeller-type rotating blade 54 is used for the stirring means (rotary stirring). However, the stirring means may be configured such that a rectangular stirring piece (not shown) having a driving means such as an air cylinder tube is attached to the front end of the hydraulic rod 52a of the hydraulic cylinder 52. The stirring piece is embedded in the alloy raw material powder p, and reciprocates horizontally at a predetermined cycle level to extend over the entire length of the cavity 2 2 in the radial direction (horizontal stirring). When the stirring or horizontal stirring is performed, the hydraulic rod 52a can be moved up and down, so that the stirring piece can be moved up and down. The alloy raw material powder p in the cavity 22 is stirred and mixed as a whole. In addition, the rotating blade 5 4 used in the rotary stirring method is capable of causing the alloy to be agitated. The configuration in which the powder P is stirred and mixed as a whole is not particularly limited, and a configuration in which a gas flow is stirred may be employed. However, the shape is preferably a shape in which it is difficult to cause the alloy raw material powder P to be pulverized during stirring. As shown in Fig. 8, For the rotating blade, for example, a substantially L-shaped plate 5 4 a may be used to offset the paddle blade type provided on the rotating shaft at an angle of 90 degrees [refer to Fig. 8 (a)], or a screw provided by rotating the blade 54b. a blade type [refer to Fig. 8 (b)], or an anchor blade type having a plate piece 54c extending parallel to the rotation axis [refer to Fig. 8 (c)], and then rotating the number according to the selected type of rotating blade And the stirring time is appropriately set. On the other hand, the stirring means is not limited to the rotary stirring or the horizontal stirring. The gas nozzle may be attached to the front end of the hydraulic rod 5 2 a, and the stirring means may be formed by a non-magnetic material to be intermittent or continuous. The high-pressure gas is injected to agitate the alloy raw material powder P in the cavity 22. Further, this embodiment describes a configuration in which powder molding is performed using the uniaxial pressure type molding apparatus 1-18-200916236. However, the present invention is not limited thereto, and the molding apparatus may be formed of a hydrostatic type of a rubber mold (not shown). In this case, the alloy raw material powder P is filled in a rubber mold for constituting the charging chamber, and then The agitating device 5 performs an orientation step of agitation in a magnetic field. On the other hand, the molded body obtained by the molding step of the one-axis pressure molding device 1 can be re-formed using a hydrostatic molding device to perform the second molding. In this way, it is possible to reduce cracking or breakage of the molded body. In the present embodiment, the alloy raw material powder is kneaded in a magnetic field using a molding device 1 and magnetic field oriented to form an oriented body, and then, In the case where a magnetic field is applied, compression molding is performed to produce a molded body. For example, the alloy raw material powder obtained by the above may be filled with a Mo-made case having an opening formed thereon, and the stirring device 5 may perform a predetermined time in a magnetic field. After stirring out of the stirring device 5, the demagnetization is not performed, but the Mo cap is mounted on the upper opening of the case, and the magnetic field is weakened. 'Will be attached to the lid of the box is directly sintered into a sintering furnace produced the permanent magnet (sintered body). In this case, 'the intensity of the magnetic field is set to I2k0e', the cube is formed into a cube of 7 cm, the number of rotations of the stirring device 5 is set to 40,000 rpm, and the stirring time is set to 2 seconds, whereby the sintered body obtained is Br = 1.51. kG, (BH) max = 55.1MG0e, an average magnet characteristic with a degree of orientation of 99% can be obtained. In addition, the present embodiment has been described by taking the manufacture of a sintered magnet as an example. However, as long as the powder which is polarized in a magnetic field or an electric field is not oriented to produce an oriented body, the oriented body is compression-molded. The molding apparatus 1 of the present invention is disclosed in the above-mentioned -19-200916236. For example, the specified powder is molded in a magnetic field and then sintered into fT to form a sintered body of nitriding sand (S i 3 N 4 ). BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a view showing the state of a standby position of a molding apparatus for carrying out a manufacturing method of the present invention. Fig. 2 is an operation explanatory view of the molding apparatus shown in Fig. 1. Fig. 3 is an explanatory view showing the operation (orientation step) of the molding apparatus shown in Fig. 1. Fig. 4(a) is a magnetic field orientation explanatory diagram of a prior art, and Fig. 4(b) is an explanatory diagram of a stirring magnetic field orientation of the present invention. Fig. 5 is an explanatory view showing the operation (forming step) of the molding apparatus shown in Fig. 1. Figure 6 is an explanatory diagram of the pulsating pulse magnetic field. Fig. 7 is an explanatory diagram showing a modification of the pulsating pulse magnetic field. Fig. 8(a) to Fig. 8(c) are views showing other forms of the rotary vane used in the stirring device. [Description of main component symbols] 1 : Compression molding machine 2 : Mold 2 1 : Through hole 22 : Mold groove 3 1 , 3 2 : Punch -20- 200916236 4 : Magnetic field generating device 5 : Stirring device 54 : Rotating blade 56 : cover P: alloy raw material powder