200821392 九、發明說明： 【發明所屬之技術領域】 本發明有關於含有釓的鎂合金，且尤其有關於具有高 強度，耐腐蝕，及強度與延性的最佳平衡者。該合金作為 鎂合金使用時也具有極高的溫度性能。本發明的合金已研 發出作為擠壓合金，但也能捲曲以製造薄板且也適用於鍛 造及機械加工。雖然其能成功的鑄造以形成鋼坏，但是這 些合金在一些製程中不適於作為成形合金使用，這些製程 如模鑄或沙鑄如其它鎮合金，這是因為易於形成裂痕。 【先前技術】 關於鎂釔釓（Mg-Y-Gd)系統有許多先前技術。 如美國專利339103號教示可製造出一種二元合金， 其含有鎂及8-11重量％的釔，該合金可隨著時間而變硬。 它指出這些合金的延性與其軟化強度成反比，及可接 受的延性是大於3-5%。它教示在鎂釔系統中，小於8重量 %的釔位準，與其它鎂合金相比，不能產生足夠的機械特 性。 美國專利339103號所述的機械特性如表一所示。 表一 釔含量（重量 軟化應力 UTS(Mpa) 伸長％ °/〇) (Mpa) 8· 2 303 344 3 9. 0 323 374 6 6 200821392 10.6 335 374 5 俄國專利SU1010880號教示一種含有釔及釓，也可含 有錯的鎂合金。該專利所述的二種特定合金具有的機械特 性如表二所示。 表二 合金組成（重量％) 軟化應力（Mpa) UTS(Mpa) 伸長％ 4-6%紀，8-10%釓，3-1· 〇8%鎂 ' : ------- 378-390 393-442 4.4-9.8 5_6· 5% 釔 ，4. 5-5. 5% 1，〇· 15-〇· 7%锆 353-387 397-436 4.0-6.0 此先前技術教示這些類型的含鎂合金於鑄造時會產 生裂痕，但是藉由以鍅取代鎂可減少此效應，關於這些合 金的腐姓特性或各向同性，此先前技術則並未教示。 日本專利JP10147830號教示一種合金，含有1-6重 量％的釓及6-12重量％的釔，在高溫下可產生良好的強度， 也可存在高達2重量％的锆。 日本專利JP9263871號也教示一種合金，含有0.8-5 重量％的釔及4—15重量％的釓或鏑，可製造出一種產品， 其能鍛造以製造出良好強度的合金。惟’此先前技術並未 了解，各合金元素的量的重要性，以及其個別比例的重要 性。 使用峰值硬度作為測量，在合金上執行一些測試，該 合金具有一定值的原子比例烯土（總烯土）元素，同時改變 釔加上其它可溶性鋼化物與乳之比，結果如以下所示： 7 200821392 熔號 原子％釓 原子％纪及 其它可溶性 鑭化物 原 子 %TRE 釔及其 它可溶 性鑭化 物與釓 之比 釓重量 % 重量％釔及 其它可溶性 鑭化物 峰硬度 DF9122 1. 33 2. 00 3· 33 1.5 7. 6 6. 5 127 DF9123 0.83 2. 50 3. 33 3. 0 4· 8 8. 2 110 DF9124 2. 50 0. 83 3.33 0· 3 13. 1 2. 6 118 日本專利JP9263871號也討論加入鈣及其它鑭化物， 但是我們已發現，加入舞及其它鑭化物對於這些類型的合 金疋極為不好的。200821392 IX. INSTRUCTIONS OF THE INVENTION: TECHNICAL FIELD OF THE INVENTION The present invention relates to magnesium alloys containing niobium, and in particular to an optimum balance of high strength, corrosion resistance, and strength and ductility. The alloy also has extremely high temperature properties when used as a magnesium alloy. The alloy of the present invention has been developed as an extruded alloy, but can also be crimped to produce a sheet and is also suitable for forging and machining. Although they can be successfully cast to form steel defects, these alloys are not suitable for use as forming alloys in some processes, such as die casting or sand casting, such as other town alloys, because cracks are easily formed. [Prior Art] There are many prior art techniques for the magnesium-niobium (Mg-Y-Gd) system. As taught in U.S. Patent No. 3,393,103, a binary alloy containing magnesium and 8-11% by weight of cerium can be produced which can harden over time. It states that the ductility of these alloys is inversely proportional to their softening strength, and the acceptable ductility is greater than 3-5%. It teaches that in the magnesium lanthanum system, less than 8% by weight of the ruthenium level does not produce sufficient mechanical properties compared to other magnesium alloys. The mechanical properties described in U.S. Patent No. 339,103 are shown in Table 1. Table 1 钇 content (weight softening stress UTS (Mpa) elongation % ° / 〇) (Mpa) 8· 2 303 344 3 9. 0 323 374 6 6 200821392 10.6 335 374 5 Russian patent SU1010880 teaches a kind of 钇 and 釓, It may also contain a wrong magnesium alloy. The mechanical properties of the two specific alloys described in this patent are shown in Table 2. Table 2 Alloy composition (% by weight) Softening stress (Mpa) UTS (Mpa) Elongation % 4-6%, 8-10% 釓, 3-1· 〇8% magnesium ' : ------- 378- 390 393-442 4.4-9.8 5_6· 5% 钇, 4. 5-5. 5% 1, 〇 · 15-〇 · 7% zirconium 353-387 397-436 4.0-6.0 This prior art teaches these types of magnesium Alloys can be cracked during casting, but this effect can be reduced by replacing magnesium with niobium, which is not taught in the prior art regarding the rot properties or isotropy of these alloys. Japanese Patent No. JP 10147830 teaches an alloy containing 1-6 wt% of bismuth and 6-12 wt% of ruthenium, which can produce good strength at high temperatures, and can also have up to 2 wt% of zirconium. Japanese Patent No. JP9263871 also teaches an alloy containing 0.8 to 5% by weight of niobium and 4 to 15% by weight of niobium or tantalum to produce a product which can be forged to produce a good strength alloy. However, this prior art does not understand the importance of the amount of each alloying element and the importance of its individual proportions. Using peak hardness as a measure, some tests were performed on the alloy, which had a certain atomic ratio of olefinic (total olefinic) elements, while changing the ratio of cerium plus other soluble slag to milk, the results are as follows: 7 200821392 Melt atom % 釓 atom % and other soluble telluride atoms % TRE 钇 and other soluble tellurides to 釓 釓 % % % 钇 钇 钇 钇 钇 DF9122 1. 33 2. 00 3· 33 1.5 7. 6 6. 5 127 DF9123 0.83 2. 50 3. 33 3. 0 4· 8 8. 2 110 DF9124 2. 50 0. 83 3.33 0· 3 13. 1 2. 6 118 Japanese Patent JP9263871 Discussions have been made to add calcium and other tellurides, but we have found that the addition of dance and other tellurides is extremely undesirable for these types of alloys.
中國專利CN1676646教示更廣範圍的合金，其含有u 重里％的紀’6-15重量％的亂，〇·35-0.8重量％的結，及0—1.5 重量％的鈣，可擠壓該合金以製造出具有良好強度的擠製 πσ彳一疋在其合金範例中對此的敘述極少，而且並無明確 的顯示該合金在接近要求範圍極限的應用。 所有的這些先前技術似乎只注意使合金強度極大因 而犧牲其延性，而後者是同等重要的材料特性。此外，先 前技術也不了解不同合金元素的位準對於上述合金的腐 2為的效應。本發日錄示—種方式以得载㈣延性， 達成㊅強度位準’又不犧牲抗腐祕。上述先前技 ‘;、：：？當至少二種鑭化物及釔在相同合金中，其原子 ，辰度的特纽是添加物是否有效社要因素。 藉由在本發㈣請專·財選擇合金添加物及控 8 200821392 制合金的各向同性，除了這些改良的機械特性以外，本發 明的合金在工業標準ASTI B117鹽霧测試中，大致將具有 小於每年100米耳（mpy)的腐姓率，且較佳小於50mpy。由 於這些先前技術未提及該等合金的的腐蝕特性，所以也可 假設該等合金的此特性與習知合金相同，強度低於本發明 合金的腐触率及大於5Ompy的腐姓率。Chinese patent CN1676646 teaches a wider range of alloys, which contain 6% to 6% by weight of u, 〇·35-0.8% by weight of knots, and 0 to 1.5% by weight of calcium, which can be extruded The production of extruded πσ彳 疋 with good strength is very rare in its alloy examples, and there is no clear indication that the alloy is close to the required range. All of these prior art techniques seem to only pay attention to the fact that the strength of the alloy is greatly compromised by its ductility, which is an equally important material property. Furthermore, the prior art does not understand the effect of the level of the different alloying elements on the rot of the above alloy. This is the day of the record - a way to get (four) ductility, to achieve six strength levels' without sacrificing anti-corruption. The above prior art ‘;,::? When at least two kinds of tellurides and bismuth are in the same alloy, the atomicity and the end of the nucleus are the effective factors of the additive. In addition to these improved mechanical properties, the alloy of the present invention is substantially tested in the industry standard ASTI B117 salt spray test by selecting the alloy additive in the present invention (4) and controlling the isotropy of the alloy. It has a decay rate of less than 100 meters per year (mpy), and is preferably less than 50 mpy. Since these prior art do not mention the corrosion characteristics of the alloys, it is also assumed that the properties of the alloys are the same as those of the conventional alloys, the strength is lower than the corrosion rate of the alloy of the present invention and the corrosion rate of more than 5 Ompy.
尤其是在Rokhl in所寫的學術著作，即名稱是「含有 烯土金屬的鎂合金」一書中，作者Rokhlin，L L，2003 年出版，俄國專利SU1010880號的發明人指出增加鎂合金 的釔含量對於合金的腐蝕率是不良的，如表三所示。該專 利指出這是因為有Mg24Y5複合物 ，其對於固態溶液是陰極的。 表三 釔含量 腐蝕率 重量％ mg/cm2/ 小時 米 耳/年 0· 5 0. 025 48 3.8 0. 14 268 10. 5 0. 36 690 【發明内容】 根據本發明而提供一種鎂合金，其由以下組成：2.0 9 200821392 至5. 0原子％，較隹是2· 3至4· 6原子％的釓，及至少一元 素，其選自可溶性重鑭化物及紀組成之群中，其中可溶性 重鑭化物及釔總量與亂量之比在1· 25:1與1. 75:1之間， 且較佳大約是1.5:1，從〇至0.3原子％的锆，較佳是具有 至少0· 03原子％的鋅，其中當存在鋅時，鋅與锆的重量之 比較佳小於2:1，及更佳小於0.75·· 1，所有的其它鑭化物， 如鑭，鈽，镨，鈥，鉅，釤，銪及釔，其總量小於〇· 2原Especially in the academic work written by Rokhl in, the name "magnesium alloy containing olefinic metals", author Rokhlin, LL, published in 2003, the inventor of Russian patent SU1010880 pointed out that increasing the niobium content of magnesium alloys The corrosion rate for the alloy is poor, as shown in Table 3. The patent states that this is due to the presence of the Mg24Y5 complex which is cathodic to the solid solution. Table 3 钇 content corrosion rate weight % mg / cm 2 / hour meter / year 0 · 5 0. 025 48 3.8 0. 14 268 10. 5 0. 36 690 SUMMARY OF THE INVENTION According to the present invention, a magnesium alloy is provided, The composition consists of: 2.0 9 200821392 to 5.0 atomic %, which is 23 to 4.6 atomic % of yttrium, and at least one element selected from the group consisting of soluble heavy bismuth compounds and complexes, wherein soluble The ratio of the total amount of ruthenium compound and ruthenium to the amount of ruthenium is between 1:25:1 and 1.75:1, and preferably about 1.5:1, and from zirconium to 0.3 atom% of zirconium, preferably at least 0·03 atom% of zinc, wherein when zinc is present, the weight of zinc and zirconium is preferably less than 2:1, and more preferably less than 0.75··1, all other tellurides such as lanthanum, cerium, lanthanum, cerium , giant, 钐, 铕 and 钇, the total amount is less than 〇· 2 original
子％ ’及較佳小於0 · 1原子％ ’鎮是平衡者，而任何其它元 素的重量不大於0.2原子％，及較佳不大於〇. 1原子％，及 更佳其存在只是意外的雜質。 【實施方式】 在本說明書中，可溶性重鑭化物定義為具有原子量65 至69(含）及71的元素。可溶性重鑭化物（SHL)是指那些在 鎂中顯示顯著固體可溶度者。它們是铽，鏑，鈥，铒，鍤 及镏。這些元素的特徵是其都具有相同的六角緊密配置的 2屬結構，如釔及鎂具有的，及具有〇· 178⑽至〇· i73nm 此屬i徑。當氧化時’其也僅存在於三價狀態，如 價而2/、二匕元素如銪及鏡不同，該銪及镱具有三價及雙 在鎂+残示任何顯著的_可溶度。當出現時， 的:械=!總位準應該大於°，1原子%以對於合金 物是_。 的貢獻。—種特別的較佳可溶性重鑭化 的量====== 200821392 百分比（不是重量百分比）表示的矩陣中溶解）的量有關， 以及與藉由加熱處理以沈澱中間顆粒的電位有關。用於釔 及鎂以及用於釓及鎂的可溶性重鑭化物及鎂的雙相圖，都 顯示此電位。由這些相位圖可假設可溶性重鑭化物，釓及 釔都可以類似方式增加鎂的強度。惟，令人驚奇發現的 是，當乳以特定量存在時，在一定範圍中添加可溶性重鑭 化物或釔，會形成至少一中間三相，其影響合金的機械特 性。此至少一個三相需要可溶性重鑭化物或釔與釓間之比 是3:2。具有此例的合金，與使用鑭化物，纪及亂量的其 它組合所能達成的相比，顯示更佳的機械特性組合，即強 度，延性及橫向特性。可發現明顯改良的特性，其中對於 合金（其含有2. 3至4. 6原子％的釓總量及至少一可溶性重 鑭化物或紀）該比在1.25:1與1.75:1之間。此範圍外的 合金強度及/或延性都下降。當釓，可溶性重鑭化物及釔 的總量低於2. 0原子％及高於5. 0原子％時，此下降最明顯。 為了有助於此沈澱硬化效應，而添加一顆粒精細元 素，其量高達其在合金中的固體可溶度極限。此元素的較 佳者是錯。可藉由增加量而添加它以大致提高合金的軟化 應力及伸長對失效等特性。對於此一效應，應該存在至少 0. 03原子百分比的锆，而極大量是合金中鍅的固體可溶度 極限，其大致約是0. 3原子百分比。惟，錘的高及低位準 抗腐餘力會下降。含有本發明合金的錯的最佳組成是5.5 至6.5重量％的釔，6.5至7.5重量％的釓，及0.2至0.4 重量％的錯，而剩餘者是鎂及意外雜質。至於某些合金組 11 200821392 f，結的位準應該從G. 3至低於〇. 35重量％， 鹽霧測試。 ^ ^UmPy 是右Z現存在少量的鋅對於本發明合金的抗腐餘特性 ^的，但是鋅位準增加後會劣化合金的抗腐 車又锃的，鋅的位準應該從0·07至低於〇 5 改The sub-% 'and preferably less than 0 · 1 atom%' town is the balancer, and the weight of any other element is not more than 0.2 atom%, and preferably not more than 〇. 1 atom%, and better, its existence is only an unexpected impurity. . [Embodiment] In the present specification, a soluble heavy bismuth compound is defined as an element having an atomic weight of 65 to 69 inclusive and 71. Soluble heavy bismuth compounds (SHL) are those which show significant solid solubility in magnesium. They are 铽, 镝, 鈥, 铒, 锸 and 镏. These elements are characterized in that they all have the same hexagonal tightly arranged 2 genera structure, such as those of strontium and magnesium, and have 〇·178(10) to 〇· i73nm. When oxidized, it also exists only in the trivalent state, such as valence and 2/, diterpene elements such as ruthenium and mirrors, which have trivalent and bis-magnesium and any significant _ solubility in magnesium. When present, the :machine=! total level should be greater than °, 1 atomic % is _ for the alloy. Contribution. - A particularly preferred amount of soluble deuteration ====== 200821392 The percentage (not by weight) is related to the amount of dissolution in the matrix, and to the potential of the intermediate particles by heat treatment. This potential is shown for the biphasic diagrams of strontium and magnesium as well as soluble heavy bismuth and magnesium for strontium and magnesium. From these phase diagrams it can be assumed that soluble heavy bismuth, lanthanum and cerium can increase the strength of magnesium in a similar manner. Surprisingly, however, it has been found that when the milk is present in a specific amount, the addition of soluble heavy bismuth or bismuth in a range results in at least one intermediate three phase which affects the mechanical properties of the alloy. The at least one three phase requires a soluble heavy bismuth or the ratio of bismuth to bismuth is 3:2. Alloys of this type exhibit a better combination of mechanical properties, i.e., strength, ductility and lateral properties, as compared to other uses of telluride, and other combinations of chaos. Significantly improved properties can be found in which the ratio is between 1.25:1 and 1.75:1 for the alloy (which contains 2.3 to 4.6 atomic percent total ruthenium and at least one soluble heavy ruthenium or yttrium). Alloy strength and/or ductility outside this range are reduced. This decrease is most pronounced when the total amount of soluble heavy bismuth and bismuth is less than 2.0 atomic % and above 0.5 atomic %. To aid in this precipitation hardening effect, a particulate fine element is added in an amount up to its solid solubility limit in the alloy. The better of this element is wrong. It can be added by increasing the amount to substantially increase the softening stress of the alloy and the properties such as elongation versus failure. The atomic percentage of the cerium in the alloy is about 0.3 atomic percent. However, the high and low level of the hammer will reduce the residual strength. The optimum composition of the alloy containing the present invention is 5.5 to 6.5% by weight of ruthenium, 6.5 to 7.5% by weight of ruthenium, and 0.2 to 0.4% by weight of the error, with the remainder being magnesium and unexpected impurities. For some alloy groups 11 200821392 f, the level of the knot should be from G. 3 to less than 〇. 35 wt%, salt spray test. ^ ^UmPy is the right Z present a small amount of zinc for the corrosion resistance of the alloy of the present invention, but the increase in zinc level will degrade the alloy's anti-corrosion car, the level of zinc should be from 0. 07 to Less than 〇5
2·^ /:的’以及已發現鋅與锆之比應該不超過 •及應"亥較佳的小於〇· 75:1。 1 在二、ίΐ可溶性重鑭化物或釔以外的任何鑭化物，t存 在的總量應該^[、於^ n Q @ 1 π人， 〜评 0/ ^ 於〇· 2原子百分比，及較佳低於〇· 1原 0 ’否則會干擾期望的上述至少一中 、子 66 , , 〒間二相的形成。類似 二任何，、匕元素存在的量不該超過〇·2原子％，較佳 不超過0·1原子％，及更佳的是只出現在意外雜質的仅準。 其本發月的合金可用於擠壓，板金，板及鍛造。或者， /、可用於些兀件，其從擠壓，板金，板或鍛造中加工 /或製造出。 久 範例 在含有3·〇4原子％的釔及釓總量中製造出鎂合 _791 ’ &中紀與I之比是1·52··1。此外，它含有〇 15 原子%的八錄，而其它元素在雜質位準。 在5有2. 65原子％的釔及釓總量中製造出另一鎂合金 8961其中紀與釓之比是1· 46:1。此外，它含有〇. 原子％的#及〇·〇8原子％的鋅，而其它元素在雜f位準。 在含有3· 〇3原子％的铒，釓及釔混合物中製造出另— 12 200821392 鎂合金DF9380，其具有可溶的烯土元素加上纪與IL之比是 1.38:1。此外，它含有0.125原子％的鍅。· 所有的這些具有大於300MPa的軟化應力，及大於或等 於10%的伸長對失效；。 測試另外三個鎂合金，即合金DF8915，DF9386及 DF8758，其具有的釔及釓總位準類似於DF8961的，但是 比例不同。DF8915具有3.9:1的明顯高比例，而且它僅產 生250MPa的減少軟化應力。DF9386及DF8758都分別具有 0.72:1及0·93:1的明顯低比例。這些低比例的效用是減 少這些合金的延性至低於5%的位準，而這是市面銷售的這 類產品不能接受的。 在含有2· 99原子％的镱，釓及釔混合物中製造出又一 鎂合金DF9381，其具有可溶的烯土元素加上紀與亂之比是 1· 39·· 1。此外，它含有〇· 121原子％的錯。此合金中的鏡 不是可溶性重鑭化物，而將它加入合金的結果是減少合金 強度至不能接受的低位準。 製造又一組測試合金以檢查錯對於本發明合金的腐 勉。溶化DF9382a至DF9382e，其都具有相同的組成，除 了不同的錘位準以外。合金DF9382a顯示若材料無鍅（即 在私準工業火花發射光譜下可測到的極限），在標準鹽霧 測试中，腐蝕率是高於可接受的每年腐蝕5〇米耳位準。 此外，用於此合金的高錯位準中，DF9382b及DF9382C也 顯不此極差的行為。惟，在〇· 〇3原子％(〇· i重量幻與〇· 12 原子％(0.4重量％)之間的锆位準，可達成良好的抗腐蝕 13 200821392 性，此如DF9382d及DF9382e所顯示的。 這些測試結果如以下表四所示，其中部分資料已四捨 五入02·^ /:' and it has been found that the ratio of zinc to zirconium should not exceed • and should be better than 〇· 75:1. 1 In the second, ΐ ΐ soluble heavy bismuth or any bismuth other than bismuth, the total amount of t should be ^ [, ^ n Q @ 1 π person, ~ 0 / ^ 〇 · 2 atomic percentage, and better Below 〇·1 original 0' would otherwise interfere with the formation of the above-mentioned at least one neutron, 66, and interphase. Similar to any of the two, the amount of the lanthanum element should not exceed 〇·2 atom%, preferably not more than 0.1 atom%, and more preferably only occurs in the case of unexpected impurities. Its monthly alloys can be used for extrusion, sheet metal, sheet and forging. Alternatively, / can be used in parts that are machined/manufactured from extrusion, sheet metal, sheet or forging. For a long time, magnesium is produced in a total amount of yttrium and lanthanum containing 3 〇 4 atom%. The ratio of JI to I is 1.52··1. In addition, it contains 〇15 atomic percent of the eight records, while the other elements are at the impurity level. Another magnesium alloy was produced in 5 total of 2.65 atom% of niobium and tantalum. The ratio of the ratio of the period to the niobium was 1.46:1. In addition, it contains 〇. Atomic% of # and 〇·〇8 atom% of zinc, while other elements are at the impurity f level. In the mixture of lanthanum, cerium and lanthanum containing 3 〇 3 atomic %, another 12 200821392 magnesium alloy DF9380 having a soluble olefinic element plus a ratio of IL to 1.38:1 was produced. In addition, it contains 0.125 atom% of ruthenium. • All of these have a softening stress greater than 300 MPa and an elongation pair greater than or equal to 10% failure; The other three magnesium alloys, alloys DF8915, DF9386 and DF8758, were tested with a total ruthenium and osmium level similar to that of DF8961, but with different ratios. The DF8915 has a significantly high ratio of 3.9:1 and it only produces a softening stress of 250 MPa. Both DF9386 and DF8758 have a significantly low ratio of 0.72:1 and 0·93:1, respectively. These low ratios of utility are to reduce the ductility of these alloys to levels below 5%, which is unacceptable for products such as those sold in the market. Another magnesium alloy, DF9381, was produced in a mixture of ruthenium, osmium and iridium containing 1.9 at%, and the ratio of the soluble olefinic element to the chaos was 1.39··1. In addition, it contains 〇·121 atom% of the error. The mirror in this alloy is not a soluble heavy telluride, and the addition of it to the alloy results in a reduction in alloy strength to an unacceptably low level. A further set of test alloys was made to check for the rot of the alloy of the present invention. The DF9382a to DF9382e are melted, all of which have the same composition, except for different hammer levels. Alloy DF9382a shows that if the material is flawless (ie, the limit measurable under the private industrial spark emission spectrum), the corrosion rate is higher than the acceptable annual corrosion level of 5 〇 meters in the standard salt spray test. In addition, DF9382b and DF9382C also exhibit this extremely poor behavior in the high misalignment of this alloy. However, in the zirconium level between 原子·〇3 atom% (〇·i weight illusion and 〇·12 atom% (0.4% by weight), good corrosion resistance 13 can be achieved, as shown by DF9382d and DF9382e. The results of these tests are shown in Table 4 below, some of which have been rounded to zero.
表四Table 4
14 20082139214 200821392
熔號 分析 ’ 拉力特性 腐飩 釔 其它 釓 锆 總 重 1 1 1 1 1 i 1 1 1 V ； 重 鑭 鑭 重 原 重 原 重量 原子 重 原子 化 化 0.2% UTS %E1 MPY 量 子 量 子％ % % 量 % 物+ 物+ MPa MPa % % % % 釔+ 釔： 釓 釓 DF8791 6 1.8 7 1.3 0.5 0.15 3.05 1.52 317 444 10 Zn Zn DF8961 5.2 1.57 0.2 0.08 6.3 1.08 0.4 0.12 2.65 1.46 308 424 17 Er Er DF9380 5.09 1.55 0.94 0.15 7.72 1.33 0.42 0.125 3.03 1.38 306 409 13 DF8915 8.1 2.44 3.7 0.63 0.5 0.15 3.07 3.9 250 356 13 DF9386 5.13 1.64 12.64 2.286 0.24 0.075 3.93 0.72 359 450 3.5 DF8758 4.7 1.45 8.9 1.55 0.4 0.12 3.0 0.93 319 433 3.9 Yb Yb DF9381 5.18 1.58 1.0 0.16 7.28 1.25 0.41 0.121 2.99 1.39 264 367 15 DF9382a 6 ；1.8 i 7 13 0 ：〇 3 1.5 5 8 DF9382b 6 ；,s ; 7 ; 1.3 0.41 1 1 i 0.13 3 1.5 5 8 DF9382c 6 ! ι.8 I I [ 7 ; 1.3 0.5 ;0.147 3 1.5 285 DF9382d 6 ΐ 1.8 ； 7 ; 1.3 * _ 0.33 > ；0.098 3 1.5 17 ； ； ； J ； DF9382e 6 ：1.8 ! 7 ：1.3 1 0.24 ：0.071 3 1.5 9Melt analysis 'tension characteristic rot other 釓 zirconium total weight 1 1 1 1 1 i 1 1 1 V ; heavy 重 heavy original weight atom heavy atomization 0.2% UTS %E1 MPY quantum quantum % % % %物+物+ MPa MPa % % % % 钇+ 钇: 釓釓DF8791 6 1.8 7 1.3 0.5 0.15 3.05 1.52 317 444 10 Zn Zn DF8961 5.2 1.57 0.2 0.08 6.3 1.08 0.4 0.12 2.65 1.46 308 424 17 Er Er DF9380 5.09 1.55 0.94 0.15 7.72 1.33 0.42 0.125 3.03 1.38 306 409 13 DF8915 8.1 2.44 3.7 0.63 0.5 0.15 3.07 3.9 250 356 13 DF9386 5.13 1.64 12.64 2.286 0.24 0.075 3.93 0.72 359 450 3.5 DF8758 4.7 1.45 8.9 1.55 0.4 0.12 3.0 0.93 319 433 3.9 Yb Yb DF9381 5.18 1.58 1.0 0.16 7.28 1.25 0.41 0.121 2.99 1.39 264 367 15 DF9382a 6 ;1.8 i 7 13 0 :〇3 1.5 5 8 DF9382b 6 ;,s ; 7 ; 1.3 0.41 1 1 i 0.13 3 1.5 5 8 DF9382c 6 ! ι. 8 II [ 7 ; 1.3 0.5 ; 0.147 3 1.5 285 DF9382d 6 ΐ 1.8 ; 7 ; 1.3 * _ 0.33 >; 0.098 3 1.5 17 ; ; ; J ; DF9382e 6 : 1.8 ! 7 : 1.3 1 0.24 : 0.071 3 1.5 9