201202435 六、發明說明： 【發明所屬之技術領域】 本發明涉及常溫用高強度/高延伸率鎂合金及其製造 方法。 【先前技術】 目前，工業上廣泛使用Mg-A1類合金。若在Mg合金 中添加A1 ’則因A1所引起的高溶強化及因p_Mgl7All2相 的形成所引起的粒界強化，Mg合金的強度變大，熔點變 低，流動性變大，從而變得更適合壓鑄。但因爲脆性大的 β相的增加’將降低其柔軟性。若要將鎂合金用於汽車部 件等’則不能在受到衝擊時立即斷裂，而需吸收衝擊能量 保持原狀’從而在常溫下需要高的柔軟性。而且，隨柔軟 性的增加，也可確保加工性及產品成型性能。 因此，爲了確保強度和鑄造性，需要開發一種M g - A1 類合金’其在維持高水準的A1添加比率的同時，具備高水 準的柔軟性。柔軟性的提高，一般會犧牲強度。若柔軟性 的提高導致強度的降低’則將會限制合金的應用範圍，因 此，難以達到合金商用化的目的。 因此，需同時考慮柔軟性和強度。若要提高Mg-A1合 金的柔軟性’則需添加與M g或A1的反應性強的元素，從 而形成新的相，以抑制脆性大的β相。 【發明内容】 本發明的目的在於提供一種常溫用鎂合金及其製造方 法’其向鎂或鎂合金的金屬溶液添加鹼土金屬氧化物（尤其 201202435 是氧化鈣），以製造鎂合金。 另外，本發明的另一目的在於提供一種常溫用錶合金 及其製造方法，其向鎂合金添加鹼土金屬氧化物’即Ca0 ’ 以減少氧化物、夾雜物、氣孔等，提高鑄件的內部完整性’ 從而同時提高其柔軟性及強度。 本發明的目的不受如上所述目的的限制’而對於本領 域的普通技術.人員而言，未提及的其他技術目的從下麵的 說明中變得顯而易見。 爲達到上述目的，本發明常溫用鎂合金製造方法’包 括如下步驟：熔化鎂或鎂合金；向熔化有上述鎂或鎂合金 的金屬溶液表面添加0.05〜1.2wt%的CaO;藉由表面攪拌消 耗CaO，以藉由上述金屬溶液和所添加的上述CaO的充分 反應，使CaO基本上不殘留於反應物中；及使上述去除氧 成分的Ca充分反應，從而使其基本上不殘留於上述鎂或鎂 合金中。 · 具體而言，上述所添加的CaO量爲0.2wt%至0.9wt%， 而較佳地，上述所添加的C a Ο量爲〇 . 3 w t %至0.7 w t %。 因添加上述CaO所生成的化合物有Mg2Ca或Al2Ca或 (Mg、Al)2Ca中的至少一種。 爲達到上述目的’本發明常溫用鎂合金，其特徵在於： 向鎂或鎂合金的金屬溶液添加0.05〜1.2 wt %的CaO之後， 藉由上述金屬溶液和所添加的上述CaO的還原反應，消耗 上述CaO的一部分或全部’以使Ca和上述鎂類合金中的 M g兀素或構成口金的其他兀素結合生成化合物，從而使合 201202435 金的常溫機械物性大於添加CaO之前的鎂或鎂合金的常溫· 機械物性。 具體而言，上述常溫機械物性是指常溫屈服強度、常 溫拉伸強度或常溫延伸率中的一種。 隨上述CaO的添加量的增加，合金的常溫機械物性增 加；隨上述CaO的添加量的增加，合金的常溫屈服強度或 常溫拉伸強度和常溫延伸率同時增加。 上述所添加的CaO量爲0.2wt%至0.9 wt%，而較佳地， 上述所添加的CaO量爲0.3wt%至〇.7wt%:而因添加上述 CaO所生成的化合物有Mg2Ca或.Al2Ca或（Mg、Al)2Ca中 的至少一種。 如上所述，本發明向商用鎂合金中添加CaO，從而使 鎂合金的組織變細並形成Al2Ca相等。另外，抑制脆性大 的P_Mg17Al12相的形成，大幅減少鑄造缺陷。結果，藉由 添加CaO，同時提高鎂合金的強度和柔軟性。 【實施方式】 下面，結合附圖對本發明較佳實施例進行詳細說明。 在附圖中，在任何地方對相同的結構儘量使用相同的標 記。另外，省略對有可能給本發明的技術思想帶來混淆的 已公開功能及結構的說明。 本發明涉及將氧化鈣添加於錶金屬溶液而製造新合金 的方法及利用上述方法製造而成的合金，而所要解決的技 術課題是將上述鈣添加於鎂時的問題並克服物性的限制。 圖1爲本發明鎂類合金製造方法順序圖。 201202435 如圖1所示，本發明鎂合金製造方法，包括如下步驟： 形成鎂類金屬溶液S1;添加鹼土金屬氧化物（在本發明中爲 氧化鈣CaO)S2 ;攪拌S3 ;消耗鹼土金屬氧化物S4 ;進行 鹼土金屬反應（在本發明中爲鈣C a) S5;鑄造S6;及固化 S7。上述消耗鹼土金屬氧化物的步驟S4和上述進行鹼土金 屬反應的步驟S5，雖然爲了說明的便利而分爲單獨的步 驟，但兩個工序S4、S5幾乎同時發生。即，若在S4步驟 中開始供應鹼土金屬，則開始S 5步驟。 在上述形成鎂類金屬溶液的步驟S1，在將鎂或鎂合金 投入熔爐之後，在保護氣體氣氛下提供400至8 00 °C的溫 度。則上述熔爐內的鎂合金經熔化成爲鎂類金屬溶液。 鎂或鎂合金的熔化溫度 在本發明中，鎂或鎂合金的熔化解溫度是指純鎂金屬 熔化的溫度和鎂合金熔化的溫度。根據合金種類的不同， 熔化溫度有可能存在差異。爲進行充分的反應，在鎂或鎂 合金完全被熔化的狀態下投入氧化鈣。鎂或鎂合金的熔化 溫度，只要是能使固態充分熔化成完全的液態的溫度即 可。但在本發明中，考慮到氧化鈣的投入會降低金屬溶液 的溫度，需在有充分餘量的溫度範圍內維持金屬溶液的作 業。 在此，若溫度低於400 °C，則難以形成鎂合金金屬溶 液，而若溫度高於800雙聲道，則存在可使鎂類金屬溶液 燃燒的危險。另外，雖然在上述鎂的情況下，大致在600°C 以上的溫度形成金屬溶液，但在鎂合金的情況下，也可在 201202435 4 0 0〜6 0 0 °C之間的溫度形成金屬溶液。一般而言，在金屬學 上，大多情況下隨著形成合金其熔點將降低。 若熔化溫度過高，則將發生液體金屬的氣化，而且， 根據鎂的特點容易燃燒，因此’可導致金屬溶液量的損失， 且也給最終物性帶來不利的影響。 用於上述鎂類金屬溶液形成步驟的鎂，可爲從純鎂、 鎂合金及其等價物中選擇的任何一種。另外，上述鎂合金 可爲從 AZ91D、AM20、AM30、AM50、AM60、AZ31、AS41、 AS31、 AS21X、 AE42、 AE44、 AX5卜 AX52、 AJ50X、 AJ52X、 A J6 2X、MRI1 5 3、MRI23 0 ' AM-HP2 ' Mg-Al ' Mg-Al-Re ' Mg-Al-Sn、Mg-Zn-Sn、Mg-Si、Mg-Zn-Y 及其等價物中選 擇的任何一種，但本發明不受這些鎂合金的限制。可選用 通常用於工業的任何鎂合金。 在上述添加鹼土金屬氧化物的步驟S2，向上述鎂金屬 溶液添加粉末狀的氧化鈣。在此，爲促進與鎂合金的反應， 氧化鈣以粉末狀爲宜。 氧化鈣的粉末狀態 爲進行反應而投入的氧化鈣，可以任何形式投入。但 爲了有效的反應，取可增加反應表面積的粉末狀爲宜。但 是’若小於0.1 wn，則因氣化的鎂或熱風飛散，從而不易 投入到爐中》另外，相互凝聚，不易與液態的熔融金屬混 合並結塊。但若過大，則因不利於增加表面積而不可取。 理想的粉末粒度爲小於5 00卿以下爲宜。而更加爲200卿 以下。 201202435 而爲了防止粉末相的飛散’也可投入凝聚粉末的九狀 氧化鈣。 所投入的鹼土金屬氧化物（氧化鈣） 作爲向金屬溶液添加的鹼土金屬氧化物，本發明使用 氧化鈣（CaO)。此外，也可爲從SrO、BeO或 MgO及其等 價物中選擇的至少一種。 用於上述添加鹼土金屬氧化物的步驟的鹼土金屬氧化 物，一般可添加0.001至30 wt%。 鹼土金屬氧化物的投入量取決於最終目標合金的成 分。即，根據鎂合金中所要包含的Ca的量，藉由逆計算決 定CaO的量。若鎂合金中從CaO間接包括Ca的量超過 2 1 . 4 w t % ( C a Ο爲3 0 w t % )，則鎂合金的物性將超出原來的物 性，因此，上述投入量需在低於30.0 wt%的範圍內調節。 在本發明中，用作鹼土金屬氧化物的氧化鈣的投入量 爲0 · 0 5 w t %至1 · 2 w t %。在氧化鈣的投入量低於1 . 2 w t %時， 可獲得優秀的常溫高強度（拉伸強度/屈服強度）和優秀的常 溫高延伸率的物性値。但若氧化鈣的投入量低於0.05 wt %， 則上述物性値的改善效果相對較小。較佳地，上述氧化鈣 的投入量爲 〇.2wt%至 〇.9wt%。而更加爲 0.3wt%至 0 · 7 w t °/p在氧化鈣的投入量爲0 · 3 w t %至0.7 w t %範圍內時， 可獲得優秀的常溫高強度/高延伸率的物性値。與此同時， 在 0.3wt%至 〇.7wt%的範圍內，常溫機械物性値（拉伸強 度、屈服強度、延伸率），隨氧化鈣的量的增加而增加。 在上述攪拌步驟S3，以1秒〜60分鐘/所添加的氧化鈣 201202435 O.lwt%的標準，攪拌上述鎂金屬溶液。 在此，若攪拌時間少於1秒/0 · 1 wt% ’則不能氧化錦充 分混合至鎂金屬溶液，而若攪拌時間多餘60分鐘/0· lwt% ’ 則造成鎂金屬溶液的攪拌時間的浪費。一般而言’攪拌時 間取決於金屬溶液的量和所投入的氧化銘的量。 在投入氧化物粉末時’可採用一次性投入的方法’也 可爲促進反應，降低粉末的凝聚可能性’採用第—次投入 之後經過一定時間之後再次投入的方法，或採用分爲適當 兩依次投入的方法。 攪拌方法及條件 爲本發明鎂或鎂合金和氧化鈣的有效反應’進行攪拌 爲宜。一般的攪拌方法是在盛有金屬溶液的爐周圍具備可 施加電磁場的裝置，以藉由產生電磁場引起金屬溶液的對 流。另外，也可從外部人爲地對金屬溶液進行攪拌（機械攪 拌）。若進行機械攪拌，可進行適當攪拌以防止所投入的氧 化鈣粉末凝聚。在本發明中，攪拌的最終目的是幫助金屬 溶液和所投入的粉末的還原反應。 根據金屬溶液的溫度和所投入的粉末的狀態（預熱狀 態）等，攪拌時間可存在差異。較佳地，原則上攪拌至在金 屬溶液表面看不見粉末爲止。其原因是，因粉末的比重比 金屬溶液小，因此，在正常狀態下粉末將漂浮於金屬表面 之上，而若在金屬溶液表面看不見粉末，則可間接判斷已 充分反應。在此，充分反應是指氧化鈣基本上都與金屬溶 液反應而被消耗的狀態。 201202435 即使在金屬溶液表面看不見粉末，但也不能排出其存 在於金屬溶液之中的可能性，因此，在經過攪拌時間之後， 有可能在維持一定時間的同時，確認是否存在未來得及浮 上的粉末，以完全消耗還未反應的粉末。 攪拌時機 攪拌的時機以在投入氧化物粉末的同時進行爲宜。另 外，也可在氧化物從金屬溶液獲得熱量以達到一定溫度以 上之後，開始攪拌以促進反應。直至看不見投入至金屬溶 液表面的氧化物粉末爲止進行攪拌。氧化鈣藉由反應完全 消耗之後結束攪拌。 表面反應 一般而言，若向金屬溶液直接添加鹼土金屬中的 Ca 和S r，則因比重的差異，從而向重較小的鎂的金屬溶液下 沉的同時完成反應。因此，只藉由攪拌金屬溶液，即可幫 助C a的熔化，生成合金。 與此相反，若向金屬溶液投入氧化鈣，則同樣因比重 的差異，不向金屬溶液下沈而在金屬溶液表面漂浮。 通常，在生成合金時，藉由在金屬溶液和金屬之間形 成對流（convection)或對其進行攪拌（stirring)，促進積極的 反應，幫助金屬溶液內部的反應。但是，在本發明中，若 促進反應，則因投入金屬溶液的氧化物來不及反應而殘留 於最終的材料之中，從而成爲降低物性値或導致缺陷的原 因。即’若促進非金屬溶液表面的金屬溶液內部的反應， 則不能促進金屬溶液表面的反應，從而最終使氧化鈣殘留 -10- 201202435 於金屬溶液之中相對較多。 因此，在本發明中，需創造一種反應條件，以使氧化 物在非金屬溶液內部的金屬溶液表面進行反應。爲此，需 不將漂浮於金屬溶液表面的氧化物，強制攪拌進金屬溶液 內部。較佳地，在暴露於空氣的金屬溶液的表面，將鹼土 金屬氧化物均勻鋪開。更加地，在供應氧化物時，用氧化 物塗布金屬溶液的全部表面。 較之不進行攪拌，進行攪拌更能促進反應，而較之在 金屬溶液的內部進行攪拌，在外部表面（上層部表面）進行 攪拌更能促進反應。即，金屬溶液在外部表面（上層部表面） 更好地與露出至空氣中的氧化物粉末進行反應。真空或氣 氛氣體環境下的結果不是很好。爲了充分的‘反應，需藉由 上層部攪拌促進表面反應。在此，充分的反應是指所投入 的驗土金屬氧化物全部與金屬溶液反應，從而基本上不殘 留於金屬溶液中的反應。在本發明中，該促進表面的攪拌 稱之爲表面攪拌。即，藉由添加至Mg金屬溶液的表面的 CaO的還原反應（表面還原反應）生成的Ca，將作爲Mg或 Mg合金的元素。 下表1爲在向AM60B鎂合金金屬溶液各添加5、10、 1 5wt%的7 0卿粒子大小的氧化鈣之後，按不同的攪拌方法 測得的鎂合金內的氧化鈣殘餘量。攪拌方法分金屬溶液的 上部層攪拌、金屬溶液的內部攪拌及其餘的未攪拌。此時， 對上部層的攪拌在從上述金屬溶液表面位元於全部金屬溶 液深度的1 〇 %左右的上部層進行。根據不同的攪拌條件， -11 - 201202435 只對上部層進行攪拌的情況，較之未攪拌情況和進行內部 攪拌的情況’在各添加5、1 0、1 5 w t %的氧化纟5的情況下， 氧化鈣的殘餘量分別爲0.001、0.002、0.005wt %，其殘留 量最少。即，爲了使CaO在Mg金屬溶液表面進行表面而 對金屬溶液上部層進行攪拌的情況下，所添加的絕大部分 CaO分離爲Ca。即，向商用AM60B的合金添加CaO，以 藉由還原反應向合金添加Ca。 表1201202435 VI. Description of the Invention: [Technical Field of the Invention] The present invention relates to a high strength/high elongation magnesium alloy for normal temperature and a method for producing the same. [Prior Art] Currently, Mg-A1 type alloys are widely used in the industry. When A1' is added to the Mg alloy, the high-solubility strengthening due to A1 and the grain boundary strengthening due to the formation of the p_Mgl7All2 phase increase the strength of the Mg alloy, lower the melting point, and increase the fluidity, thereby becoming more Suitable for die casting. However, because of the increase in the fragile β phase, the softness will be lowered. If a magnesium alloy is used for an automobile part or the like, it cannot be broken immediately after being subjected to an impact, and it is necessary to absorb the impact energy to maintain the original state, thereby requiring high flexibility at normal temperature. Moreover, as the flexibility increases, workability and product forming properties are also ensured. Therefore, in order to secure strength and castability, it is required to develop an alloy of M g - A1 which has a high level of flexibility while maintaining a high level of A1 addition ratio. The increase in softness generally results in a sacrifice of strength. If the increase in flexibility results in a decrease in strength, the range of application of the alloy will be limited, and thus it is difficult to achieve commercialization of the alloy. Therefore, it is necessary to consider both softness and strength. In order to increase the flexibility of the Mg-A1 alloy, it is necessary to add an element having high reactivity with Mg or A1, thereby forming a new phase to suppress the β phase having a large brittleness. SUMMARY OF THE INVENTION An object of the present invention is to provide a magnesium alloy for normal temperature and a method for producing the same, which adds an alkaline earth metal oxide (especially 201202435 is calcium oxide) to a metal solution of magnesium or a magnesium alloy to produce a magnesium alloy. Further, another object of the present invention is to provide a table alloy for normal temperature and a method for producing the same, which comprises adding an alkaline earth metal oxide 'Ca0' to a magnesium alloy to reduce oxides, inclusions, pores, etc., and improve the internal integrity of the casting. ' Thereby increasing its softness and strength. The object of the present invention is not limited by the above-described objects, and other technical objects not mentioned will become apparent to those skilled in the art from the following description. In order to achieve the above object, the method for producing a magnesium alloy for normal temperature according to the present invention includes the steps of: melting a magnesium or a magnesium alloy; adding 0.05 to 1.2% by weight of CaO to the surface of the metal solution in which the magnesium or magnesium alloy is melted; and consuming by surface agitation CaO is such that CaO does not substantially remain in the reactant by the sufficient reaction of the above metal solution and the added CaO; and Ca of the oxygen-removing component is sufficiently reacted so as not to remain substantially in the magnesium Or in magnesium alloys. Specifically, the amount of CaO added is 0.2% by weight to 0.9% by weight, and preferably, the amount of C a added as described above is 〇 3 w t % to 0.7 w %. The compound formed by adding the above CaO may be at least one of Mg2Ca or Al2Ca or (Mg, Al) 2Ca. In order to achieve the above object, the magnesium alloy for normal temperature of the present invention is characterized in that: after adding 0.05 to 1.2 wt% of CaO to the metal solution of magnesium or magnesium alloy, the reduction is carried out by the reduction reaction of the above metal solution and the added CaO described above. A part or all of the above CaO is such that Ca and MG in the above magnesium alloy or other alizarin constituting gold are combined to form a compound, so that the mechanical properties of the 201202435 gold at room temperature are greater than those of the magnesium or magnesium alloy before the addition of CaO. Normal temperature and mechanical properties. Specifically, the above-mentioned room temperature mechanical property refers to one of normal temperature yield strength, normal temperature tensile strength, or room temperature elongation. As the amount of CaO added increases, the mechanical properties of the alloy increase at room temperature; as the amount of CaO added increases, the room temperature yield strength or the normal temperature tensile strength and the room temperature elongation increase simultaneously. The amount of CaO added is 0.2% by weight to 0.9% by weight, and preferably, the amount of CaO added is 0.3% by weight to 7.7% by weight: and the compound formed by adding the above CaO is Mg2Ca or .Al2Ca Or at least one of (Mg, Al) 2Ca. As described above, the present invention adds CaO to a commercial magnesium alloy to make the microstructure of the magnesium alloy thin and form Al2Ca equal. Further, formation of a P_Mg17Al12 phase having a large brittleness is suppressed, and casting defects are greatly reduced. As a result, the strength and softness of the magnesium alloy are simultaneously improved by adding CaO. [Embodiment] Hereinafter, preferred embodiments of the present invention will be described in detail with reference to the accompanying drawings. In the drawings, the same reference numerals are used as much as possible for the same structure anywhere. In addition, the description of the disclosed functions and structures that may confuse the technical idea of the present invention is omitted. The present invention relates to a method of producing a new alloy by adding calcium oxide to a surface metal solution and an alloy produced by the above method, and the technical problem to be solved is to solve the problem of adding calcium to magnesium and to overcome physical properties. Fig. 1 is a sequence diagram showing a method for producing a magnesium-based alloy of the present invention. 201202435 As shown in FIG. 1, the method for producing a magnesium alloy of the present invention comprises the steps of: forming a magnesium-based metal solution S1; adding an alkaline earth metal oxide (in the present invention, calcium oxide CaO) S2; stirring S3; consuming an alkaline earth metal oxide S4; performing an alkaline earth metal reaction (in the present invention, calcium C a) S5; casting S6; and curing S7. The step S4 of consuming the alkaline earth metal oxide and the step S5 of performing the alkaline earth metal reaction described above are divided into separate steps for convenience of explanation, but the two steps S4 and S5 occur almost simultaneously. That is, if the supply of the alkaline earth metal is started in the step S4, the step S 5 is started. In the above step S1 of forming a magnesium-based metal solution, after the magnesium or magnesium alloy is introduced into the furnace, a temperature of 400 to 800 ° C is supplied under a protective gas atmosphere. Then, the magnesium alloy in the above furnace is melted into a magnesium-based metal solution. Melting Temperature of Magnesium or Magnesium Alloy In the present invention, the melting temperature of the magnesium or magnesium alloy means the temperature at which the pure magnesium metal is melted and the temperature at which the magnesium alloy is melted. Depending on the type of alloy, there may be differences in the melting temperature. In order to carry out a sufficient reaction, calcium oxide is supplied in a state where the magnesium or magnesium alloy is completely melted. The melting temperature of the magnesium or magnesium alloy is as long as it can sufficiently melt the solid state into a completely liquid state. However, in the present invention, in consideration of the fact that the input of calcium oxide lowers the temperature of the metal solution, it is necessary to maintain the operation of the metal solution in a temperature range having a sufficient margin. Here, if the temperature is lower than 400 °C, it is difficult to form a magnesium alloy metal solution, and if the temperature is higher than 800 double channels, there is a risk that the magnesium metal solution can be burned. Further, in the case of the above magnesium, a metal solution is formed at a temperature of approximately 600 ° C or higher, but in the case of a magnesium alloy, a metal solution may be formed at a temperature between 201202435 4 0 0 to 600 ° C. . In general, in metallography, in most cases, the melting point of the alloy will decrease as the alloy is formed. If the melting temperature is too high, vaporization of the liquid metal occurs, and it is easy to burn according to the characteristics of magnesium, so that the amount of the metal solution can be lost, and the final physical properties are adversely affected. The magnesium used in the above magnesium metal solution forming step may be any one selected from pure magnesium, magnesium alloy and equivalents thereof. Further, the above magnesium alloy may be from AZ91D, AM20, AM30, AM50, AM60, AZ31, AS41, AS31, AS21X, AE42, AE44, AX5, AX52, AJ50X, AJ52X, AJ6 2X, MRI1 5 3, MRI23 0 ' AM -HP2 'Mg-Al 'Mg-Al-Re 'Mg-Al-Sn, Mg-Zn-Sn, Mg-Si, Mg-Zn-Y and any equivalent thereof, but the invention is not subject to these magnesium Alloy limitations. Any magnesium alloy commonly used in industry can be used. In the step S2 of adding the alkaline earth metal oxide described above, powdered calcium oxide is added to the above magnesium metal solution. Here, in order to promote the reaction with the magnesium alloy, calcium oxide is preferably in the form of a powder. Powder state of calcium oxide Calcium oxide which is supplied for the reaction can be supplied in any form. However, in order to carry out an effective reaction, it is preferred to take a powder which increases the surface area of the reaction. However, if it is less than 0.1 wn, the vaporized magnesium or hot air is scattered, so that it is not easily put into the furnace. In addition, it is agglomerated with each other and is not easily mixed with liquid molten metal to form agglomerates. However, if it is too large, it is not desirable because it is not conducive to increasing the surface area. The ideal powder particle size is preferably less than 500 qing. And more than 200 qing. 201202435 In order to prevent the scattering of the powder phase, it is also possible to introduce agglomerated calcium pentoxide. The alkaline earth metal oxide (calcium oxide) to be charged is used as the alkaline earth metal oxide added to the metal solution, and calcium oxide (CaO) is used in the present invention. Further, it may be at least one selected from the group consisting of SrO, BeO or MgO and its equivalent. The alkaline earth metal oxide used in the above step of adding an alkaline earth metal oxide can be generally added in an amount of 0.001 to 30% by weight. The amount of the alkaline earth metal oxide to be added depends on the composition of the final target alloy. Namely, the amount of CaO is determined by inverse calculation based on the amount of Ca to be contained in the magnesium alloy. If the amount of Ca indirectly from CaO in the magnesium alloy exceeds 21.4 wt% (C a Ο is 30 wt%), the physical properties of the magnesium alloy will exceed the original physical properties, therefore, the above input amount needs to be lower than 30.0. Adjust within the range of wt%. In the present invention, the amount of calcium oxide used as the alkaline earth metal oxide is from 0. 5 5 w t % to 1 · 2 w t %. When the amount of calcium oxide is less than 1.2 w %, excellent room temperature and high strength (tensile strength/yield strength) and excellent room temperature and high elongation physical properties can be obtained. However, if the amount of calcium oxide is less than 0.05 wt%, the effect of improving the above physical properties is relatively small. Preferably, the amount of the calcium oxide is from 〇. 2wt% to 9.9wt%. Further, when the input amount of calcium oxide is from 0.3 wt% to 0 · 7 w t ° / p in the range of 0 · 3 w t % to 0.7 w t %, excellent normal temperature high strength / high elongation physical properties can be obtained. At the same time, in the range of 0.3 wt% to 7.7 wt%, the mechanical properties at room temperature (tensile strength, yield strength, elongation) increase as the amount of calcium oxide increases. In the stirring step S3, the magnesium metal solution is stirred for 1 second to 60 minutes/calcium oxide 201202435 O.lwt%. Here, if the stirring time is less than 1 second / 0 · 1 wt% ', the oxidized bromine can not be sufficiently mixed to the magnesium metal solution, and if the stirring time is more than 60 minutes / 0 · lwt% ', the stirring time of the magnesium metal solution is caused. waste. In general, the amount of agitation depends on the amount of metal solution and the amount of oxidation that is invested. When the oxide powder is put in, the method of 'one-time input can be used' can also promote the reaction and reduce the possibility of agglomeration of the powder, and the method of re-injecting after a certain period of time after the first input is adopted, or The method of input. Stirring method and conditions It is preferred to stir the effective reaction of the magnesium or magnesium alloy of the present invention with calcium oxide. A general agitation method is to provide a device for applying an electromagnetic field around a furnace containing a metal solution to cause convection of the metal solution by generating an electromagnetic field. Alternatively, the metal solution may be artificially stirred (mechanically stirred) from the outside. If mechanical agitation is carried out, appropriate agitation may be performed to prevent the calcium oxide powder to be agglomerated. In the present invention, the ultimate purpose of the agitation is to assist in the reduction reaction of the metal solution and the powder to be charged. The stirring time may vary depending on the temperature of the metal solution and the state of the powder to be charged (preheated state) and the like. Preferably, it is stirred in principle until no powder is visible on the surface of the metal solution. The reason is that since the specific gravity of the powder is smaller than that of the metal solution, the powder will float on the metal surface under normal conditions, and if the powder is not visible on the surface of the metal solution, it can be indirectly judged to have sufficiently reacted. Here, the sufficient reaction means a state in which calcium oxide is substantially consumed by reacting with a metal solution. 201202435 Even if the powder is not visible on the surface of the metal solution, the possibility of its presence in the metal solution cannot be discharged. Therefore, after the stirring time, it is possible to confirm whether there is a powder that can be floated in the future while maintaining a certain period of time. To completely consume the unreacted powder. Stirring timing The timing of stirring is preferably carried out while the oxide powder is being charged. Alternatively, after the oxide is heated from the metal solution to reach a certain temperature or higher, stirring is started to promote the reaction. Stirring was carried out until the oxide powder charged on the surface of the metal solution was not visible. The calcium oxide is stirred after the reaction is completely consumed. Surface reaction In general, when Ca and S r in an alkaline earth metal are directly added to a metal solution, the reaction is completed while sinking to a metal solution having a small weight due to a difference in specific gravity. Therefore, the melting of C a can be assisted only by stirring the metal solution to form an alloy. On the other hand, when calcium oxide is introduced into the metal solution, it also floats on the surface of the metal solution without sinking to the metal solution due to the difference in specific gravity. Generally, in the formation of an alloy, a positive reaction is promoted by convection or stirring between the metal solution and the metal to assist the reaction inside the metal solution. However, in the present invention, when the reaction is promoted, the oxide of the metal solution is not required to react and remains in the final material, which is a cause of deterioration of physical properties or defects. That is, if the reaction inside the metal solution on the surface of the non-metal solution is promoted, the reaction on the surface of the metal solution cannot be promoted, and finally the calcium oxide residue -10- 201202435 is relatively large among the metal solutions. Therefore, in the present invention, it is necessary to create a reaction condition for allowing the oxide to react on the surface of the metal solution inside the non-metal solution. For this reason, it is necessary to forcibly stir the oxide floating on the surface of the metal solution into the inside of the metal solution. Preferably, the alkaline earth metal oxide is evenly spread over the surface of the metal solution exposed to the air. Further, when the oxide is supplied, the entire surface of the metal solution is coated with the oxide. The stirring is more effective than the stirring, and the stirring is carried out on the outer surface (the upper surface) to promote the reaction as compared with the stirring inside the metal solution. That is, the metal solution is better reacted on the outer surface (upper layer surface) with the oxide powder exposed to the air. The results in a vacuum or atmosphere are not very good. In order to fully react, the surface reaction is promoted by stirring the upper layer. Here, the sufficient reaction means a reaction in which all of the applied earth metal oxides are reacted with the metal solution so as not to remain substantially in the metal solution. In the present invention, the agitation of the promoting surface is referred to as surface agitation. That is, Ca produced by a reduction reaction (surface reduction reaction) of CaO added to the surface of the Mg metal solution is an element of Mg or a Mg alloy. Table 1 below shows the residual amount of calcium oxide in the magnesium alloy measured by different stirring methods after adding 5, 10, 15 wt% of calcium oxide having a size of 70 g to each of the AM60B magnesium alloy metal solution. The stirring method is divided into the upper layer of the metal solution, the internal stirring of the metal solution, and the rest without stirring. At this time, the agitation of the upper layer was carried out in an upper layer from the surface of the above metal solution to about 1 〇% of the total metal solution depth. Depending on the mixing conditions, -11 - 201202435 only stirs the upper layer, compared to the case of no stirring and internal stirring 'in the case of adding 5, 10, 1 5 wt % of yttrium oxide 5 The residual amount of calcium oxide is 0.001, 0.002, 0.005 wt%, respectively, and the residual amount is the least. That is, in the case where CaO is stirred on the surface of the Mg metal solution to agitate the upper layer of the metal solution, most of the added CaO is separated into Ca. Namely, CaO is added to the alloy of the commercial AM60B to add Ca to the alloy by a reduction reaction. Table 1
添加5wt% 的CaO 添加10wt% 的CaO 添加 15wt0/〇 的CaO 合金內CaO 殘餘量 未攪拌 4.5wt% CaO 8.7wt% CaO 13.5wt% CaO 金屬溶液內部攪拌 l_2wt% CaO 3.lwt% CaO 5.8wt% CaO 金屬溶液上部層攪拌 (本發明） 0.00lwt% CaO 0.002wt% CaO 0.005wt% CaO 氧化鈣的氧成分藉由上述對金屬溶液上部層的攪拌， 基本上從金屬溶液表面去除。上述攪拌在從上述金屬溶液 表面位元於全部金屬溶液深度的20%左右的上部層進行爲 宜。在20%以上的深度，不能產生作爲本發明較佳實施例 的表面反應。而較佳地，上述攪拌在從上述金屬溶液表面 位元於全部金屬溶液深度的10%左右的上部層進行爲宜。 這是藉由控制使漂浮的氧化鈣基本上位於金屬溶液深度 1 0%的上部層，以最大限度地減少金屬溶液的擾亂。 在上述消耗鹼土金屬氧化物的步驟S4,藉由上述金屬 溶液和上述所添加的氧化鈣的反應，使氧化鈣至少一部分 或基本上（substantially)不殘留於鎂合金中。在本發明中， 所投入的氧化鈣藉由充分的反應全部消耗爲宜。但是，即 -12- 201202435 使存在一部分未反應而殘留於合金內的氧化鈣，需不能對 物性產生很大的影響。 在此，消耗氧化鈣是指從鹼土金屬氧化物中去除氧成 分。上述氧成分可以氧（〇2)氣體的形式去除，或藉由與金 屬溶液中的鎂或其合金成分的結合，以浮渣（dross)或沉澱 物形式去除。在此，氧化鈣所提供的C a，較之合金內的 Mg，更傾向於與其他的成分元素化合。另外，上述氧成分 藉由對金屬溶液上部層的攪拌，基本上從金屬溶液表面去 除。 圖3爲在本發明中，藉由對鎂金屬溶液上部層的攪拌 使氧化鈣（CaO)解離的模式圖。 在上述進行驗土金屬反應的步驟S5，使藉由上述消耗 氧化鈣而生成的鈣進行反應，以使鈣至少一部分或基本上 不殘留於鎂合金中。在此，藉由消耗而生成的鈣，與上述 鎂合金中的鎂、鋁或上述金屬溶液中的其餘合金元素（成分） 中的至少一種化合，以基本上不殘留於鎂合金中。在此， 化合物是指藉由金屬和金屬的結合而生成的金屬間化合 物。 在本發明中，消耗全部所投入的氧化鈣時，其效果達 到最佳。可藉由金屬溶液和氧化鈣的充分反應，使氧化銘 不殘留於鎂合金中。金屬溶液中不殘留上述氧化鈣時，其 機械物性値達到最高。若因某些原因氧化鈣未藉由反應全 部消耗’而只消耗其中的一部分’則較之全部消耗的情況， 其物性値較低。但即使是消耗一部分的情況，其物性値優 -13- 201202435 於相同成分的未投入氧化鈣的鎂合金的物性。 結果’所添加的氧化錦，藉由與作爲金屬溶液的鎂合 金的反應’至少一部分或基本上去除氧成分，而去除氧成 分的鈣’與上述鎂合金中的鎂、鋁或上述金屬溶液中的其 餘合金元素中的至少一種化合，以至少一部分或基本上不 殘留於鎂合金中。 在上述消耗鹼土金屬的步驟S5，在進行鹼土金屬氧化 物的還原反應時，在金屬溶液表面產生閃光。而這種閃光 可稱爲判斷是否結束還原反應的標誌。若在產生閃光的過 程中出鐵而結束反應，則所添加的鹼土金屬氧化物有可能 沒有完全消耗。即，在作爲還原反應的間接判斷標誌的閃 光結束之後再出鐵。 至今爲止說明的過程，如圖1和圖2所示。圖2爲在 本發明中，添加於鎂金屬溶液中的氧化鈣（CaO)的解離順序 圖。 另外，在鑄造步驟S6，將上述鎂金屬溶液倒入常溫或 預熱狀態的模具中進行鑄造。在此，上述模具爲從金屬模 具、陶瓷模具、石墨模具及其等價物中選擇的至少一種。 另外，鑄造方式可採用重力鑄造、連續鑄造及其等價方式。 在上述固化步驟S 7，將上述模具冷卻至常溫之後，從 模具中取出鎂合金（例如鎂合金鑄錠）。 藉由上述製造方法製造而成的鎂類合金的硬度（HRF) 可爲40至80。但上述硬度値根據加工方法及熱處理等的 不同存在各種變化，因此’本發明鎂類合金不受上述硬度 -14- 201202435 値的限制。 右爲純錶金屬彳谷液’則金屬溶液中的錶成分與鹼土金 屬進行反應而生成鎂（驗土金屬）化合物。在本發明中，因 鹼土金屬氧化物爲CaO，因此，生成Mg2Ca。另外，原來 構成CaO的氧，或變成〇2排出至金屬溶液外，或與1^8結 合生成MgO’從而以浮渣形式排出（請參考下面的反應式 1) 〇 反應式1Adding 5 wt% of CaO Adding 10 wt% of CaO Adding 15 wt0/〇 of CaO alloy CaO residual amount without stirring 4.5 wt% CaO 8.7 wt% CaO 13.5 wt% CaO metal solution internal stirring l_2 wt% CaO 3.lwt% CaO 5.8 wt% CaO metal solution upper layer agitation (present invention) 0.001 wt% CaO 0.002 wt% CaO 0.005 wt% CaO The oxygen component of calcium oxide is substantially removed from the surface of the metal solution by agitation of the upper layer of the metal solution described above. The agitation is preferably carried out in an upper layer from the surface of the metal solution to about 20% of the depth of the entire metal solution. At a depth of 20% or more, a surface reaction which is a preferred embodiment of the present invention cannot be produced. Preferably, the agitation is carried out in an upper layer from the surface of the metal solution to about 10% of the depth of the entire metal solution. This is achieved by controlling the floating calcium oxide to be substantially at the upper layer of the metal solution at a depth of 10% to minimize the disturbance of the metal solution. In the above-described step S4 of consuming an alkaline earth metal oxide, at least a part or substantially no calcium oxide remains in the magnesium alloy by the reaction of the above metal solution with the above-mentioned added calcium oxide. In the present invention, it is preferred that the calcium oxide to be charged is completely consumed by a sufficient reaction. However, -12-201202435, there is a part of calcium oxide which remains unreacted and remains in the alloy, and it does not have a great influence on physical properties. Here, consumption of calcium oxide means removal of an oxygen component from an alkaline earth metal oxide. The above oxygen component may be removed as an oxygen (〇2) gas or as a dross or precipitate by combination with magnesium or an alloy component thereof in the metal solution. Here, the Ca supplied by the calcium oxide is more likely to combine with other constituent elements than the Mg in the alloy. Further, the above oxygen component is substantially removed from the surface of the metal solution by stirring the upper layer of the metal solution. Fig. 3 is a schematic view showing the dissociation of calcium oxide (CaO) by stirring the upper layer of the magnesium metal solution in the present invention. In the step S5 of performing the soil-receiving metal reaction described above, the calcium produced by the above-described consumption of calcium oxide is reacted so that at least a part of the calcium or substantially does not remain in the magnesium alloy. Here, the calcium generated by the consumption is combined with at least one of magnesium, aluminum or the remaining alloying elements (components) in the above-mentioned magnesium alloy so as not to substantially remain in the magnesium alloy. Here, the compound means an intermetallic compound formed by a combination of a metal and a metal. In the present invention, when all of the calcium oxide to be charged is consumed, the effect is optimized. Oxidation is not left in the magnesium alloy by the sufficient reaction of the metal solution and the calcium oxide. When the above-mentioned calcium oxide does not remain in the metal solution, the mechanical properties are highest. If, for some reason, calcium oxide is not consumed by the reaction, and only a portion of it is consumed, the physical properties are lower than when it is consumed. However, even if it consumes a part of it, its physical properties are excellent -13-201202435. The physical properties of the magnesium alloy which is not charged with calcium oxide of the same composition. As a result, 'the added oxidized bromine, by removing at least a part or substantially removing the oxygen component from the reaction with the magnesium alloy as the metal solution, removes the calcium component of the oxygen component and the magnesium, aluminum or the above metal solution in the above magnesium alloy At least one of the remaining alloying elements is combined to remain at least partially or substantially not in the magnesium alloy. In the above-described step S5 of consuming the alkaline earth metal, when the reduction reaction of the alkaline earth metal oxide is carried out, a flash is generated on the surface of the metal solution. This kind of flash can be called a sign to judge whether or not to end the reduction reaction. If the reaction is terminated by tapping during the flashing, the added alkaline earth metal oxide may not be completely consumed. That is, iron is discharged after the end of the flash as an indirect judgment flag of the reduction reaction. The process described so far is shown in Figures 1 and 2. Fig. 2 is a dissociation sequence diagram of calcium oxide (CaO) added to a magnesium metal solution in the present invention. Further, in the casting step S6, the magnesium metal solution is poured into a mold at a normal temperature or a preheated state for casting. Here, the mold is at least one selected from the group consisting of a metal mold, a ceramic mold, a graphite mold, and the like. In addition, the casting method may employ gravity casting, continuous casting, and the equivalent thereof. After the mold is cooled to normal temperature in the above-mentioned curing step S7, a magnesium alloy (e.g., a magnesium alloy ingot) is taken out from the mold. The magnesium alloy produced by the above production method may have a hardness (HRF) of 40 to 80. However, the above hardness 値 varies depending on the processing method, heat treatment, etc., and therefore the magnesium alloy of the present invention is not limited by the above-mentioned hardness -14-201202435. On the right, the pure surface metal gluten solution is reacted with an alkaline earth metal to form a magnesium (earth-soil metal) compound. In the present invention, since the alkaline earth metal oxide is CaO, Mg2Ca is formed. Further, the oxygen which originally constitutes CaO is either 〇2 discharged to the outside of the metal solution, or is combined with 1^8 to form MgO' to be discharged as scum (refer to the following reaction formula 1) 〇 Reaction formula 1
Pure Mg + CaO -> Mg (Matrix) + Mg2Ca …[生成〇2+生成MgO浮渣] 若爲鎂金屬溶液’則金屬溶液中的鎂成分與鹼土金屬 進行反應而生成鎂（鹼土金屬）化合物或銘（驗土金屬）化合 物。另外’鎂的合金元素與鎂或鋁一起與鹼土金屬生成化 合物。在本發明中，若鹼土金屬氧化物爲CaO，則生成 Mg2Ca、Al2Ca或（Mg、A1、其他合金元素）2Ca。另外，原 來構成CaO的氧，與純鎂的情況一樣，或變成〇2排出至 金屬溶液外，或與Mg結合生成MgO，從而以浮渣形式排 出（請參考下面的反應式2)。 反應式2Pure Mg + CaO -> Mg (Matrix) + Mg2Ca ... [Formation of 〇 2+ to form MgO scum] If magnesium metal solution 'the magnesium component in the metal solution reacts with the alkaline earth metal to form a magnesium (alkaline earth metal) compound Or Ming (earth metal) compound. Further, the alloying element of magnesium forms a compound with an alkaline earth metal together with magnesium or aluminum. In the present invention, when the alkaline earth metal oxide is CaO, Mg2Ca, Al2Ca or (Mg, A1, other alloying elements) 2Ca is formed. Further, the oxygen which originally constitutes CaO, like the case of pure magnesium, is either 〇2 discharged to the outside of the metal solution or Mg is combined with Mg to form scum (refer to Equation 2 below). Reaction formula 2
Mg Alloy + CaO -> Mg Alloy (Matrix) + (Mg2Ca + Al2Ca + (Mg、A卜其他很近元素)2Ca} …[生成〇2+生成MgO浮渣] 如上所述，本發明提供比現有技術的鎂合金生產方法 更經濟的鎂合金製造工藝。鹼土金屬（例如，Ca)相對於鹼 •15- 201202435 土金屬氧化物（例如，CaO)高價的合金元素，成爲使鎂合金 價格上升的主要原因。另外，藉由利用鹼土金屬氧化物替 代鹼土金屬添加至鎂或鎂合金中，從而較容易形成合金。 與此相反，不直接添加鹼土金屬（例如，Ca)，而藉由添加 化學穩定性好的鹼土金屬氧化物（例如，CaO)，從而獲得相 同或更高的合金生成效果。即，藉由添加至Mg金屬溶液 的CaO的還原反應生成的Ca，將作爲Mg或Mg合金的元 素。 另外，若將鹼土金屬（C a)直接投入鎂或鎂合金中，則 在鎂合金中發生一定量的鹼土金屬的熔化，但若採用本發 明的技術，則在添加鹼土金屬氧化物（CaO)時，較之直接添 加鹼土金屬（C a)的情況，不發生熔化或量很少。較之直接 添加Ca，藉由CaO間接添加的方式，更容易形成包括Al2Ca 在內的金屬間化合物。因此，爲提高鎂合金的物性，需添 加一定百分比以上的鹼土金屬，但若添加鹼土金屬氧化物 製造鎂合金，則因相當量的鹼土金屬直接形成鎂或A1的金 屬間化合物（例如，Mg2Ca或Al2Ca)，從而較之直接添加 Ca ’其物性得到提高。包括Al2Ca在內的其他金屬間化合 物的形成，其約95 %以上形成於結晶粒界，而其餘約5%形 成於結晶粒內。 圖4a爲作爲比較例利用AZ9〗〇的壓鑄產品微細構造 照片’而圖4b和4c爲在本發明中，在AZ91D中添加0.3wt% 和0.7 wt%的CaO製造而成的Mg合金的壓鑄產品微細構造 照片。在本發明中，「添加CaO」是指在添加之後經過還 -16- 201202435 原反應過程。在進行冷凍室（Cold Chamber)壓鑄之後拍攝細 微構造照片。較之本發明比較例，合金的組織細緻而緻密。 這樣的傾向隨添加於Mg合金的CaO的含量的增加而變得 明顯。這是隨CaO的添加均勻分佈形成相的Al2.Ca或其他 相形成物[(Mg2Ca及（Mg、A1、其他合金元素）2Ca)]所造成 的。 圖5a至圖5d爲本發明中向AM60B合金的金屬溶液 添加0.45wt%的CaO製造而成的鎂合金的EDS成分分析 圖片。如圖所示，形成Al2Ca相並抑制P-Mg17AlI2相的形 成。 A1和Ca的存在區域的分佈也類似。即，從添加於鎂 金屬溶液的CaO分離的Ca與A1生成化合物。因此，現有 Mg-Al類合金中存在的脆性大的p-Mgl7Al12相的形成被抑 制’並提高鎂合金的柔軟性，而與此同時，藉由A12C a相 的形成，增加合金的強度。 圖6a爲商用AM60B合金，而圖6b至圖6d爲向AM60B 添加CaO製造而成的鎂合金的拉伸試片破損面SEM圖像照 片。 因合金內的氣孔等鑄造缺陷，常見酒窩（Dimple)結構 (凹陷的部分）。與此相比，添加CaO製造而成的合金（在圖 6b中向AM60B中添加〇.25wt%的CaO,在圖6c中向AM60B 中添力口 〇.58wt%的CaO，而在圖6d中向AM60B中添加 0.98 wt%的CaO)的拉伸試片破損面的酒窩結構明顯減少。 即’隨CaO的添加’合金的氣孔減少，且氧化物、夾雜物 -17- 201202435 等減少’從而減少鑄造缺陷。 圖7爲向鎂合金中添加氧化鈣時的常溫屈服強度（TYS) 圖表。而實線表示未添加CaO的AM60B合金的常溫屈服 強度。 在實施例中，向A Μ 6 0 B鎂合金添加0.2 w t %至1 . 0 w t % 範圍的氧化鈣進行了實驗。 如圖7所示，若向鎂合金中添加〇 · 3 wt%的氧化鈣，則 常溫屈服強度約爲130至137[MP a];若向鎂合金中添加 0 · 7 w t %的氧化鈣，則常溫屈服強度約爲1 5 1至1 6 8 [ Μ P a ]; 而若向鎂合金中添加0.9 wt%的氧化鈣，則屈服強度約爲 1 5 6 [ Μ P a ]。在所添加的C a Ο的量在0 · 3 w t %至0.7 w t %範圍 內時，隨C a Ο的量的增加，常溫屈服強度也一同增加。 上述隨氧化鈣wt %的屈服強度如下表2所示： 表2 合金 氧化鈣添加量 屈服強度[MPa] 0.2 〜0.3 wt% 123 ~ 137 0·3 〜0.4 wt% 131 ~ 138 0·4 〜0·5 wt% 137 ~ 142 鎂合金 0.5 〜0.6 wt% 141 ~ 161 (AM60B) 0·6 〜0.7 wt% 143 ~ 166 0.7 〜0·8 wt% 149 〜170 0.8 〜0·9 wt% 148 ~ 160 0·9 〜1 _0 wt% 148 〜158 -18- 201202435 因此’如上表2所示’在向鎂合金添加〇.7wt%的氧化 鈣的附近’常溫屈服強度（T Y S )最好。 圖8爲向鎂合金中添加氧化鈣時的常溫拉伸強度（UTS) 圖表。而實線表示未添加CaO的AM60B合金的常溫拉伸 強度。 在實施例中，向AM60B鎂合金添加〇.2wt%至l.Owt% 範圍的氧化鈣進行了實驗。 如圖8所示，若向鎂合金中添加〇.3 wt%的氧化鈣，則 常溫拉伸強度約爲205至23 0 [MPa];若向鎂合金中添加 0· 7 wt%的氧化鈣，則常溫拉伸強度約爲240至261 [MPa]; 而若向鎂合金中添加〇.9wt%的氧化鈣，則拉伸強度約爲 245至251[MPa]。在所添加的CaO的量在0.3wt%至0.7wt% 範圍內時，隨C a 0的量的增加，常溫拉伸強度也一同增加。 上述隨氧化鈣w t %的常溫拉伸強度如下表3所示： 表3 合金 氧化鈣添加量 拉伸強度[MPa] 0.2 〜〇·3 wt% 205 〜231 0.3 ~ 0.4 wt% 205 〜229 0.4 〜0.5 wt% 223 〜232 鎂合金 〇·5 ~ 〇·6 wt% 239 〜260 (AM60B) 0·6 〜0·7 wt% 240 〜260 0.7 ~ 0.8 wt% 240 〜261 〇·8 ~ 0.9 wt% 240 〜255 0.9 ~ 1.0 wt% 240 〜252 -19- 201202435 因此’如上表3所示’在向鎂合金添加〇 . 5至〇 . 8 wt% 範圍的氧化銘時，常溫拉伸強度最好。 圖9爲向鎂合金中添加氧化錦時的常溫延伸率 (elongation)圖表。而實線表示未添加CaO的AM60B合金 的常溫延伸率。 在實施例中，向AM60B鎂合金添加〇.2wt%至l.Owt% 範圍的氧化鈣進行了實驗。 如圖9所示，若向鎂合金中添加〇 . 3 w t %的氧化鈣，則 常溫延伸率約爲6至10[%]:若向鎂合金中添加〇.7wt%的 氧化鈣’則常溫延伸率約爲1 3至1 5 [ % ]:而若向鎂合金中 添加〇.9wt%的氧化鈣，則延伸率約爲13至14[%]。在所添 加的CaO的量在0.3wt%至〇.7wt%範圍內時，隨CaO的量 的增加，常溫延伸率也一同增加。 上述隨氧化鈣wt%的常溫延伸率如下表4所示： 表4 合金 氧化鈣添加量 延伸率[%] 0.2 〜0.3 wt% 6 ~ 10 0.3 〜0·4 wt% 7 ~ 12 0.4 〜0.5 wt% 12 ~ 14 鎂合金 0.5 〜0.6 wt0/〇 12 ~ 15 (AM60B) 0.6 〜0.7 wt〇/〇 13 ~ 17 0.7 〜0_8 wt% 12 〜16 0·8 〜0_9 wt% 12 〜15 0.9 〜1.0 wt% 13 ~ 14 -20- 201202435 因此，如上上表4所示，在向鎂合金添加0.5至〇.8wt % 範圍的氧化釣時，延伸率最好。 下表5表示根據本發明製造而成的鎂合金的機械特性 平均値。各資料藉由約200個實驗測量値取平均値。 表5 YS(MPa) UTS(MPa) EL(%) AM60B 115 205 6 AM60B-0.3 wt%CaO 130 220 9 AM60B-0.5wt%CaO 160 255 14 AM60B-0.7wt%CaO 165 260 14 AM60B-0.9wt%CaO 155 250 13 如圖7、圖8及圖9所示，利用添加至Mg金屬溶液的 CaO的還原反應製造而成的Mg合金，較之未添加CaO的 Mg合金，其常溫屈服強度、常溫拉伸強度及常溫延伸率都 得到提高。另外，這些常溫機械物性的提高，隨CaO的添 加量的增加而增加。而且，這些傾向在CaO的添加量在 0.3wt%至 0.7wt%時變得最明顯。這些常溫機械物性的增 加，是因爲隨CaO的添加，形成Mg2Ca或Al2Ca或（Mg、 A1) 2 C a化合物的相。 圖1〇爲比較根據本發明製造而成的鎂類合金和現有 合金的常溫屈服強度和和常溫延伸率的圖表。 如圖所示，現有的AM (添加鋁和錳的鎂合金）和AE (添 加向鋁添加稀土類金屬的鎂合金）的常溫屈服強度和常溫 延伸率成反比。 -21 - 201202435 添加CaO的鎂合金，雖然其常溫屈服強度增加，但其 常溫延伸率也增加。一般而言，如圖表的圓點（Mg-A1-RE 合金）或三角形點（Mg-A1-Μη合金）的傾向，若延伸率增加， 則合金的屈服強度將減少。即，一般而言，延伸率的增加， 將犧牲屈服強度。但如上述圖表的矩形點（添加CaO的鎂合 金）所示，若添加CaO，則隨常溫延伸率的增加，常溫屈服 強度也一同增加。 圖11爲比較在AZ91D中添加0.3wt°/。和0.7wt%的CaO 製造而成的Mg合金和未添加CaO的AZ91D Mg合金的硬 度的圖表。利用各合金進行冷凍室（Cold Chamber)壓鑄之 後，測量鉻氏硬度。添加CaO的Mg合金的硬度大於未添 加CaO的合金的硬度。另外，隨CaO添加量的增加，其常 溫硬度也增加。在本發明中，「添加CaO」是指在添加之 後經過還原反應過程。 圖12爲比較在AZ91D中添力口 0.3wt%和0.7wt%的CaO 製造而成的Mg合金和未添加CaO的AZ9 ID Mg合金的常 溫屈服強度的圖表。利用熱室（Hot Chamber)壓鑄法製造試 片之後，測量常溫屈服強度。添加CaO的Mg合金的常溫 屈服強度大於未添加CaO的合金的常溫屈服強度。較之未 添加CaO之前，添力D 0.7wt%的CaO之後，常溫屈服強度 約增加1 5%左右。另外，隨CaO添加量的增加，其常溫屈 服強度也增加。 圖13爲比較在AZ91D中添力口 0.3wt%和0.7wt%的CaO 製造而成的Mg合金和未添加CaO的AZ9 ID Mg合金的常 -22- 201202435 溫拉伸強度的圖表。利用熱室（Hot Chamber)壓鑄法製造試 片之後，測量常溫拉伸強度。 添加CaO的Mg合金的常溫拉伸強度大於未添加CaO 的合金的常溫拉伸強度。較之未添加CaO之前，添加0.7wt% 的CaO之後，常溫拉伸強度約增加14%左右。另外，隨CaO 添加量的增加，其常溫拉伸強度也增加。 圖14爲比較在AZ91D中添加〇.3wt%和0.7wt%的CaO 製造而成的Mg合金和未添加CaO的AZ9 ID Mg合金的常 溫延伸率的圖表。添加CaO的Mg合金的常溫延伸率大於 未添加CaO的合金的常溫延伸率。較之未添加CaO之前， 添加0.7wt%的CaO之後，常溫延伸率約增加三倍左右。另 外，隨CaO添加量的增加，其常溫延伸率也增加。 圖15爲表示在AZ91D中添力口 〇.3wt%和0.7wt%的CaO 製造而成的Mg合金和未添加CaO的AZ91D Mg合金的常 溫延伸率和常溫屈服強度關係的圖表。添加CaO的Mg合 金的常溫延伸率大於未添加CaO的合金的常溫延伸率。另 外，隨CaO添加量的增加，其常溫屈服強度和常溫延伸率 同時增加。 如上所述，本發明向商用鎂合金中添加CaO，從而使 鎂合金的組織變細並形成Al2Ca及Mg2Ca或（Mg、A1、其 他合金元素）2Ca相等。另外，抑制脆性大的β-ΜΕΐ7Α112相 的形成，大幅減少鑄造缺陷。結果，可藉由添加CaO利用 還原反應間接使Ca形成合金，因此，可同時增加鎂合金的 常溫強度和常溫柔軟性。 -23- 201202435 上述實施例僅用以說明本發明而非限制，本領 技術人員應當理解，可以對本發明進行修改、變 同替換’而不脫離本發明的精神和範圍，其均應 發明的申請專利範圍範圍當中。 【圖式簡單說明】 圖1爲本發明鎂類合金製造方法順序圖； 圖2爲在本發明中，添加於鎂金屬溶液中 (CaO)的解離順序圖； 圖3爲在本發明中’藉由對鎂金屬溶液上部 使氧化鈣（CaO)解離的模式圖； 圖4 a爲作爲比較例利用AZ 9 1 D的壓鑄產品 照片；圖4b和4c爲在本發明中，在AZ91D中添 和0.7wt%的CaO製造而成的Mg合金的壓鑄產品 照片； 圖5a至圖5d爲根據本發明鎂類合金製造方 成的鎂合金的ED S實驗結果照片； 圖6a至圖6d爲根據本發明製造而成的鎂合 試片破損面SEM圖像照片； 圖7爲在本發明中，爲了與不使用CaO的鎂 溫屈服強度進行比較’以不同C a Ο添加量製造而 金的常溫屈服強度測量圖表； 圖8爲在本發明中，爲了與不使用Ca〇的鎂 溫拉伸強度進行比較，以不同Ca〇添加量製造而 金的常溫拉伸強度測量圖表； 域的普通 形或者等 涵蓋在本 的氧化鈣 層的攪拌 微細構造 加 0.3wt% 微細構造 法製造而 金的拉伸 合金的常 成的鎂合 合金的常 成的鎂合 -24 - 201202435 圖9爲在本發明中，爲了與不使用CaO 溫延伸率進行比較，以不同CaO添加量製造 的常溫延伸率測量圖表； ， 圖10爲在本發明中，比較以不同CaO 成的鎂合金的常溫延伸率和常溫屈服強度和： 鎂合金的常溫延伸率和常溫屈服強度的圖表 圖1 1爲比較在A Z 9 1 D中添加0.3 w t %和 製造而成的Mg合金和未添加CaO的AZ91D 溫硬度的圖表； 圖1 2爲比較在A Z 9 1 D中添加0.3 w t %和 製造而成的Mg合金和未添加CaO的AZ91D 溫屈服強度的圖表； 圖1 3爲比較在AZ9 1 D中添加〇.3wt%和 製造而成的Mg合金和未添加CaO的AZ91D 溫拉伸強度的圖表； 圖1 4爲比較在AZ9 1 D中添加〇.3 wt%和 製造而成的Mg合金和未添加CaO的AZ91D 溫延伸率的圖表； 圖15爲表示在AZ91D中添加〇.3wt%和 製造而成的Mg合金和未添加CaO的AZ9 1D 溫延伸率和常溫屈服強度關係的圖表° 【主要元件符號說明】 Μ 〇 的鎂合金的常 而成的鎂合金 添加量製造而 不使用CaO的 » 0.7wt%的 CaO M g合金的常 0.7wt%的 CaO Mg合金的常 〇.7wt%的 CaO Mg合金的常 〇.7wt%的 CaO Mg合金的常 〇_7wt%的 CaO Mg合金的常 -25-Mg Alloy + CaO -> Mg Alloy (Matrix) + (Mg2Ca + Al2Ca + (Mg, A Bu other very close element) 2Ca} ... [Formation of 〇 2+ to form MgO scum] As described above, the present invention provides Technical magnesium alloy production method More economical magnesium alloy manufacturing process. Alkaline earth metal (for example, Ca) relative to alkali •15-201202435 The high-priced alloying element of earth metal oxide (for example, CaO) has become the main reason for the increase in the price of magnesium alloy. In addition, it is easier to form an alloy by using an alkaline earth metal oxide instead of an alkaline earth metal to be added to a magnesium or a magnesium alloy. In contrast, an alkaline earth metal (for example, Ca) is not directly added, but chemical stability is added by adding A good alkaline earth metal oxide (for example, CaO) is obtained to obtain the same or higher alloy formation effect. That is, Ca formed by a reduction reaction of CaO added to the Mg metal solution will be an element of Mg or Mg alloy. Further, when the alkaline earth metal (C a) is directly introduced into the magnesium or magnesium alloy, a certain amount of alkaline earth metal is melted in the magnesium alloy, but if the technique of the present invention is used, the alkaline earth metal is added. In the case of the compound (CaO), no melting or a small amount is formed as compared with the case where the alkaline earth metal (C a) is directly added. Compared with the direct addition of Ca, it is easier to form a metal including Al2Ca by indirect addition of CaO. Therefore, in order to improve the physical properties of the magnesium alloy, it is necessary to add a certain percentage or more of alkaline earth metal. However, if an alkaline earth metal oxide is added to produce a magnesium alloy, a relatively large amount of alkaline earth metal directly forms an intermetallic compound of magnesium or A1 (for example, , Mg2Ca or Al2Ca), thereby improving physical properties compared to direct addition of Ca'. The formation of other intermetallic compounds including Al2Ca, about 95% of which is formed in the grain boundary, and the remaining about 5% is formed in the crystal grain. Fig. 4a is a micro-structural photograph of a die-cast product using AZ9 〇 as a comparative example, and Figs. 4b and 4c are Mg alloys produced by adding 0.3 wt% and 0.7 wt% of CaO to AZ91D in the present invention. Photograph of the fine structure of the die-cast product. In the present invention, "addition of CaO" means that the original reaction process after the addition is also carried out -16-201202435. After the cold chamber is die-casting The fine structure photograph is taken. Compared with the comparative example of the present invention, the microstructure of the alloy is fine and dense. Such a tendency becomes apparent as the content of CaO added to the Mg alloy increases. This is an Al2 which forms a phase uniformly with the addition of CaO. .Ca or other phase formation [(Mg2Ca and (Mg, A1, other alloying elements) 2Ca)]. Figure 5a to Figure 5d are the manufacture of 0.45 wt% CaO in the metal solution of the AM60B alloy in the present invention. A picture of the EDS composition of the magnesium alloy. As shown, the Al2Ca phase is formed and the formation of the P-Mg17AlI2 phase is suppressed. The distribution of the presence regions of A1 and Ca is also similar. That is, Ca separated from CaO added to the magnesium metal solution forms a compound with A1. Therefore, the formation of the brittle p-Mgl7Al12 phase existing in the conventional Mg-Al alloy is suppressed and the flexibility of the magnesium alloy is improved, and at the same time, the strength of the alloy is increased by the formation of the A12Ca phase. Fig. 6a is a commercial AM60B alloy, and Figs. 6b to 6d are SEM image photographs of the tensile test piece of the tensile test piece of the magnesium alloy produced by adding CaO to AM60B. Due to casting defects such as pores in the alloy, the Dimple structure (the recessed portion) is common. In contrast, an alloy made of CaO was added (in FIG. 6b, 25.25 wt% of CaO was added to AM60B, and in Fig. 6c, AM58 wt% of CaO was added to AM60B, and in Fig. 6d The dimple structure of the damaged test piece of the tensile test piece to which 0.98 wt% of CaO was added to AM60B was remarkably reduced. That is, the pores of the 'addition of CaO' alloy are reduced, and the oxides, inclusions -17 to 201202435 are reduced, thereby reducing casting defects. Fig. 7 is a graph showing the room temperature yield strength (TYS) when calcium oxide is added to a magnesium alloy. The solid line indicates the room temperature yield strength of the AM60B alloy to which CaO is not added. In the examples, an experiment was carried out by adding calcium oxide in the range of 0.2 w t % to 1.0 w % to the A Μ 60 B magnesium alloy. As shown in Fig. 7, when 〇·3 wt% of calcium oxide is added to the magnesium alloy, the room temperature yield strength is about 130 to 137 [MP a]; if 0. 7 wt% of calcium oxide is added to the magnesium alloy, The room temperature yield strength is about 151 to 168 [ Μ P a ]; and if 0.9 wt% of calcium oxide is added to the magnesium alloy, the yield strength is about 156 [ Μ P a ]. When the amount of C a 添加 added is in the range of 0 · 3 w t % to 0.7 w t %, the room temperature yield strength also increases as the amount of C a 的 increases. The yield strength of the above calcium oxide wt% is shown in Table 2 below: Table 2 Alloy calcium oxide addition yield strength [MPa] 0.2 ~ 0.3 wt% 123 ~ 137 0·3 ~ 0.4 wt% 131 ~ 138 0·4 ~ 0 · 5 wt% 137 ~ 142 magnesium alloy 0.5 ~ 0.6 wt% 141 ~ 161 (AM60B) 0 · 6 ~ 0.7 wt% 143 ~ 166 0.7 ~ 0 · 8 wt% 149 ~ 170 0.8 ~ 0 · 9 wt% 148 ~ 160 0·9 ～1 _0 wt% 148 ～158 -18- 201202435 Therefore, as shown in Table 2 above, 'the ambient temperature yield strength (TYS) is the best in the vicinity of the addition of 7.7wt% of calcium oxide to the magnesium alloy. Fig. 8 is a graph showing the tensile strength at normal temperature (UTS) when calcium oxide is added to a magnesium alloy. The solid line indicates the room temperature tensile strength of the AM60B alloy to which CaO was not added. In the examples, experiments were carried out by adding calcium oxide in the range of 0.2% by weight to 1.0% by weight to the AM60B magnesium alloy. As shown in Fig. 8, if 〇.3 wt% of calcium oxide is added to the magnesium alloy, the tensile strength at room temperature is about 205 to 23 0 [MPa]; if 0. 7 wt% of calcium oxide is added to the magnesium alloy. The tensile strength at room temperature is about 240 to 261 [MPa]; and if y.9 wt% of calcium oxide is added to the magnesium alloy, the tensile strength is about 245 to 251 [MPa]. When the amount of CaO added is in the range of 0.3% by weight to 0.7% by weight, the tensile strength at room temperature increases as the amount of Ca0 increases. The above-mentioned tensile strength at room temperature with respect to the weight % of calcium oxide is shown in Table 3 below: Table 3 Addition amount of calcium oxide of the alloy Tensile strength [MPa] 0.2 〇·3 wt% 205 〜231 0.3 ~ 0.4 wt% 205 ～229 0.4 〜 0.5 wt% 223 ～ 232 Magnesium alloy 〇·5 ~ 〇·6 wt% 239 ～260 (AM60B) 0·6 ～0·7 wt% 240 ～260 0.7 ~ 0.8 wt% 240 ～261 〇·8 ~ 0.9 wt% 240 ~ 255 0.9 ~ 1.0 wt% 240 ~ 252 -19- 201202435 Therefore, as shown in Table 3 above, when adding 〇. 5 to 〇. 8 wt% of the range of magnesium alloy, the tensile strength at room temperature is the best. Fig. 9 is a graph showing the room temperature elongation when a oxidized bromine is added to a magnesium alloy. The solid line indicates the room temperature elongation of the AM60B alloy to which CaO is not added. In the examples, experiments were carried out by adding calcium oxide in the range of 0.2% by weight to 1.0% by weight to the AM60B magnesium alloy. As shown in Fig. 9, when 〇. 3 wt% of calcium oxide is added to the magnesium alloy, the room temperature elongation is about 6 to 10 [%]: if 〇.7 wt% of calcium oxide is added to the magnesium alloy, the room temperature is normal temperature. The elongation is about 13 to 15 [%]: and if 9 wt% of calcium oxide is added to the magnesium alloy, the elongation is about 13 to 14 [%]. When the amount of CaO added is in the range of 0.3 wt% to 7. 7 wt%, the room temperature elongation increases as the amount of CaO increases. The above-mentioned normal temperature elongation with the weight % of calcium oxide is as shown in Table 4 below: Table 4 The elongation of the addition amount of the alloy calcium oxide [%] 0.2 〜0.3 wt% 6 ~ 10 0.3 〜0·4 wt% 7 ~ 12 0.4 〜0.5 wt % 12 ~ 14 magnesium alloy 0.5 ~ 0.6 wt0 / 〇 12 ~ 15 (AM60B) 0.6 ~ 0.7 wt 〇 / 〇 13 ~ 17 0.7 ~ 0_8 wt% 12 ~ 16 0 · 8 ~ 0_9 wt% 12 ~ 15 0.9 ~ 1.0 wt % 13 ~ 14 -20- 201202435 Therefore, as shown in the above Table 4, the elongation is the best when adding an oxidation fishing in the range of 0.5 to 8% by weight to the magnesium alloy. Table 5 below shows the average mechanical properties of the magnesium alloy produced in accordance with the present invention. Each data was averaged by approximately 200 experimental measurements. Table 5 YS (MPa) UTS (MPa) EL (%) AM60B 115 205 6 AM60B-0.3 wt% CaO 130 220 9 AM60B-0.5wt% CaO 160 255 14 AM60B-0.7wt% CaO 165 260 14 AM60B-0.9wt% CaO 155 250 13 As shown in Fig. 7, Fig. 8 and Fig. 9, the Mg alloy produced by the reduction reaction of CaO added to the Mg metal solution has a room temperature yield strength and a normal temperature pull compared to the Mg alloy to which no CaO is added. Both the tensile strength and the room temperature elongation are improved. In addition, the improvement of these mechanical properties at room temperature increases as the amount of CaO added increases. Moreover, these tendencies become most apparent when the amount of CaO added is from 0.3 wt% to 0.7 wt%. The increase in these mechanical properties at room temperature is due to the formation of a phase of Mg2Ca or Al2Ca or a (Mg, A1) 2 C a compound with the addition of CaO. Fig. 1 is a graph comparing the room temperature yield strength and the room temperature elongation of a magnesium-based alloy and a conventional alloy produced according to the present invention. As shown in the figure, the conventional AM (magnesium alloy to which aluminum and manganese are added) and AE (magnesium alloy to which rare earth metal is added) are inversely proportional to the room temperature yield strength and the room temperature elongation. -21 - 201202435 The magnesium alloy added with CaO has an increase in room temperature elongation at room temperature, although its room temperature yield strength increases. In general, as in the tendency of the dot (Mg-A1-RE alloy) or the triangular point (Mg-A1-Μη alloy) of the graph, if the elongation is increased, the yield strength of the alloy will decrease. That is, in general, the increase in elongation will sacrifice the yield strength. However, as shown by the rectangular point of the above graph (magnesium alloy to which CaO is added), when CaO is added, the room temperature yield strength increases as the room temperature elongation increases. Figure 11 compares the addition of 0.3wt ° / in AZ91D. A graph of the hardness of a Mg alloy made of 0.7 wt% CaO and an AZ91D Mg alloy not added with CaO. After each alloy was subjected to die casting in a cold chamber, the chromium hardness was measured. The hardness of the Mg alloy to which CaO is added is larger than the hardness of the alloy to which CaO is not added. In addition, as the amount of CaO added increases, the room temperature hardness also increases. In the present invention, "addition of CaO" means a process of undergoing a reduction reaction after the addition. Fig. 12 is a graph comparing the room temperature yield strength of a Mg alloy produced by adding 0.3 wt% and 0.7 wt% of CaO in AZ91D and an AZ9 ID Mg alloy not containing CaO. After the test piece was produced by a hot chamber (Hot Chamber) die-casting method, the room temperature yield strength was measured. The normal temperature yield strength of the Mg alloy to which CaO is added is greater than the room temperature yield strength of the alloy to which CaO is not added. The room temperature yield strength increased by about 5% after adding CaO of 0.7 wt% before adding CaO. In addition, as the amount of CaO added increases, the room temperature yield strength also increases. Fig. 13 is a graph showing the normal tensile strength of the conventional -22-201202435 alloy of the Mg alloy produced by adding 0.3 wt% and 0.7 wt% of CaO in the AZ91D and the AZ9 ID Mg alloy not added with CaO. After the test piece was produced by a hot chamber (Hot Chamber) die-casting method, the tensile strength at room temperature was measured. The normal temperature tensile strength of the Mg alloy to which CaO is added is greater than the normal temperature tensile strength of the alloy to which CaO is not added. The tensile strength at room temperature increased by about 14% after adding 0.7 wt% of CaO before adding CaO. In addition, as the amount of CaO added increases, the tensile strength at room temperature also increases. Fig. 14 is a graph comparing the room temperature elongation of a Mg alloy produced by adding 33 wt% and 0.7 wt% of CaO to AZ91D and an AZ9 ID Mg alloy not containing CaO. The room temperature elongation of the Mg alloy to which CaO is added is larger than the room temperature elongation of the alloy to which CaO is not added. The normal temperature elongation increased by about three times after adding 0.7 wt% of CaO before adding CaO. In addition, as the amount of CaO added increases, the room temperature elongation also increases. Fig. 15 is a graph showing the relationship between the room temperature elongation and the room temperature yield strength of a Mg alloy produced by adding a weight of 3 wt% and 0.7 wt% of CaO in AZ91D and an AZ91D Mg alloy not containing CaO. The room temperature elongation of the Mg alloy to which CaO is added is larger than the room temperature elongation of the alloy to which CaO is not added. In addition, as the amount of CaO added increases, both the room temperature yield strength and the room temperature elongation increase. As described above, the present invention adds CaO to a commercial magnesium alloy to make the microstructure of the magnesium alloy fine and form Al2Ca and Mg2Ca or (Mg, A1, other alloying elements) 2Ca. In addition, the formation of a β-ΜΕΐ7Α112 phase having a large brittleness is suppressed, and casting defects are greatly reduced. As a result, Ca can be indirectly alloyed by the reduction reaction by adding CaO, and therefore, the room temperature strength and the room temperature flexibility of the magnesium alloy can be simultaneously increased. The above-mentioned embodiments are only intended to illustrate the invention and are not to be construed as limiting, and the invention may be modified and modified without departing from the spirit and scope of the invention. Within the scope. BRIEF DESCRIPTION OF THE DRAWINGS FIG. 1 is a sequence diagram of a method for producing a magnesium alloy according to the present invention; FIG. 2 is a dissociation sequence diagram of (CaO) added to a magnesium metal solution in the present invention; FIG. 3 is a view of the present invention. A schematic diagram of dissociation of calcium oxide (CaO) from the upper portion of the magnesium metal solution; Fig. 4a is a photograph of a die cast product using AZ 9 1 D as a comparative example; Figs. 4b and 4c are in the present invention, adding 0.7 in the AZ91D. Photograph of a die-cast product of a Mg alloy made of wt% of CaO; FIGS. 5a to 5d are photographs of ED S results of a magnesium alloy produced by a magnesium alloy according to the present invention; FIGS. 6a to 6d are manufactured according to the present invention; SEM image photograph of the damaged surface of the formed magnesium test piece; Fig. 7 is a comparison of the normal temperature yield strength of gold produced by the addition of different Ca Ο in order to compare with the magnesium yield strength without using CaO in the present invention. Fig. 8 is a graph showing the measurement of the normal temperature tensile strength of gold produced by different Ca 〇 addition amounts in comparison with the tensile strength of magnesium which does not use Ca 本 in the present invention; the general shape of the domain or the like is included in The stirring of the calcium oxide layer is fine Addition of a 0.3% by weight fine structure method to produce a gold-based tensile alloy of a conventional magnesium alloy - 02 - 201202435 Figure 9 is a comparison of the temperature elongation of CaO in the present invention. , the normal temperature elongation measurement chart produced by different CaO addition amounts; FIG. 10 is a comparison of the normal temperature elongation and the normal temperature yield strength of the magnesium alloy formed by different CaO in the present invention: the normal temperature elongation of the magnesium alloy and the room temperature yielding Chart of Intensity Figure 1 1 is a graph comparing the addition of 0.3 wt % of AZ 9 1 D to the manufactured Mg alloy and AZ91D without CaO; Figure 1 2 compares the addition of 0.3 wt to AZ 9 1 D % and the graph of the temperature yield strength of the manufactured Mg alloy and AZ91D without CaO added; Figure 13 is a comparison of the addition of 〇.3wt% to the AZ9 1 D and the manufactured Mg alloy and the AZ91D without the CaO added. Figure 1 is a graph comparing the temperature elongation of Mg alloy produced by adding 3.3 wt% and AZ91D without CaO added to AZ9 1 D; Figure 15 is a graph showing the addition of yttrium to AZ91D. 3wt% and manufactured Mg alloy and AZ9 1D without CaO added Graph of relationship between temperature elongation and room temperature yield strength ° [Main component symbol description] 常 〇 Magnesium alloy is often made of magnesium alloy added without CaO» 0.7wt% CaO M g alloy often 0.7wt % of CaO Mg alloys. 7% by weight of CaO Mg alloys. 7wt% of CaO Mg alloys are usually 〇7wt% of CaO Mg alloys often -25-