TWI744075B - Titanium-aluminum intermetallic and method for manufacturing the same for improving casting fluidity - Google Patents
Titanium-aluminum intermetallic and method for manufacturing the same for improving casting fluidity Download PDFInfo
- Publication number
- TWI744075B TWI744075B TW109138781A TW109138781A TWI744075B TW I744075 B TWI744075 B TW I744075B TW 109138781 A TW109138781 A TW 109138781A TW 109138781 A TW109138781 A TW 109138781A TW I744075 B TWI744075 B TW I744075B
- Authority
- TW
- Taiwan
- Prior art keywords
- titanium
- aluminum intermetallic
- casting
- fluidity
- aluminum
- Prior art date
Links
Images
Abstract
Description
本發明是有關於一種鈦鋁介金屬及其製造方法,且特別是有關於一種以改善鑄造流動性之鈦鋁介金屬及其製造方法。 The present invention relates to a titanium-aluminum intermetallic and a manufacturing method thereof, and more particularly to a titanium-aluminum intermetallic and a manufacturing method thereof for improving casting fluidity.
全球汽車產量仍在持續增長,由於降低油耗和改善城市空氣品質的要求,對低能耗高性能發動機需求量也在日益增大,渦輪增壓器能顯著提高發動機功率、改善排放、降低油耗,因而採用帶渦輪增壓器的小型發動機來替代自然吸氣的發動機是現代汽車工業的一個基本趨勢,由於渦輪葉片承受的是發動機高溫高壓的廢氣,乘用車柴油機排放廢氣溫度最高大約為850℃,而汽油機則可達1050℃,增壓器葉輪和渦輪尺寸不大,一般直徑不超過100mm,但轉速很高,最高達250000r/min,在惡劣的工作環境下連續高速工作,所以對材料和性能的要求非常高,因此開發一種高性能汽車發動機的轉子及葉片材料非常有必要。 Global automobile production is still growing. Due to the requirements for reducing fuel consumption and improving urban air quality, the demand for low-energy high-performance engines is also increasing. Turbochargers can significantly increase engine power, improve emissions, and reduce fuel consumption. The use of small engines with turbochargers to replace naturally aspirated engines is a basic trend in the modern automobile industry. Because turbine blades bear the high temperature and high pressure exhaust gas of the engine, the highest exhaust gas temperature of passenger car diesel engines is about 850°C. The gasoline engine can reach 1050℃. The size of the turbocharger impeller and turbine is not large. Generally, the diameter does not exceed 100mm, but the speed is high, up to 250,000r/min. It can work continuously at high speed under harsh working environment, so it is very important for materials and performance. The requirements are very high, so it is very necessary to develop a high-performance automotive engine rotor and blade material.
相較其他金屬間化合物而言,鈦鋁(TiAl)介金屬的綜合性能良好,其具有低密度、高熔點、高的抗氧化性以及優良的高溫強度及剛度等性質,同時鈦鋁介金屬彈性模量遠高於其它結構材料,作為結構工件使用可以明顯增進高頻振動的承受度;與鎳(Ni)基合金相比,鈦鋁介金屬又有較高的高溫抗蠕變性及良好的阻燃性能。 Compared with other intermetallic compounds, the overall performance of titanium aluminum (TiAl) intermetallic is good. It has low density, high melting point, high oxidation resistance and excellent high temperature strength and rigidity. At the same time, titanium aluminum intermetallic elasticity The modulus is much higher than other structural materials. As a structural workpiece, it can significantly improve the tolerance of high-frequency vibration. Compared with nickel (Ni)-based alloys, titanium-aluminum intermetallics have higher high-temperature creep resistance and good Flame retardant performance.
然而,動力裝置所用的渦輪葉片及渦輪轉子,像是航太發動機葉片、船用發電機葉片或車用渦輪轉子等,其大多為複雜結構的薄型零件。若使用鈦鋁介金屬做為上述薄型零件之材料,則普遍 僅能利用積層製造或是後加工技術進行該薄型零件之產品製作,故衍生製造成本高、材料損失大及加工困難度高等缺點。雖然嘗試以鑄造技術克服前述缺點並直接得到完整產品形貌,但是目前仍受限於鈦鋁介金屬因本身材料流動性較差,而導致鑄造成形不易,使得鑄造最終產品的性質不佳。 However, turbine blades and turbine rotors used in power plants, such as aerospace engine blades, marine generator blades, or vehicle turbine rotors, are mostly thin parts with complex structures. If titanium-aluminum intermetallic is used as the material of the above-mentioned thin parts, it is generally The thin parts can only be produced by using layered manufacturing or post-processing technology, so it has disadvantages such as high manufacturing cost, large material loss, and high processing difficulty. Although attempts have been made to overcome the aforementioned shortcomings by casting technology and directly obtain the complete product morphology, the current limitations of the titanium-aluminum intermetallic material are poor fluidity, which makes the casting difficult to shape, which makes the final casting product poor in properties.
因此,便有需要提供一種用以改善鑄造流動性之鈦鋁介金屬及其製造方法,以解決前述的問題。 Therefore, there is a need to provide a titanium-aluminum intermetallic for improving casting fluidity and a manufacturing method thereof to solve the aforementioned problems.
本發明之一目的是提供一種用以改善鑄造流動性之鈦鋁介金屬及其製造方法,其具有較佳的鑄造流動性。 One object of the present invention is to provide a titanium-aluminum intermetallic for improving casting fluidity and a manufacturing method thereof, which has better casting fluidity.
依據上述之目的,本發明提供一種用以改善鑄造流動性的鈦鋁介金屬,以原子百分比計算,該鈦鋁介金屬包括下列元素:Al:40~50at%、Cr:1~8at%、Nb:1~8at%、Mo:1~5at%、Mn:1~6at%、Ni+Si+Fe:1~15at%及B:0.05~0.8at%,其餘部分為Ti及不可避免之雜質。 According to the above-mentioned purpose, the present invention provides a titanium-aluminum intermetallic for improving casting fluidity. The titanium-aluminum intermetallic includes the following elements: Al: 40-50at%, Cr: 1-8at%, Nb, calculated by atomic percentage : 1~8at%, Mo: 1~5at%, Mn: 1~6at%, Ni+Si+Fe: 1~15at% and B: 0.05~0.8at%, the rest is Ti and unavoidable impurities.
本發明更提供一種用以改善鑄造流動性之鈦鋁介金屬的製造方法,包括下列步驟:一熔煉步驟:將鈦鋁介金屬之多個熔煉原料放置在一感應熔煉設備內,將該些熔煉原料熔融成一具有鑄造流動性的鈦鋁介金屬熔湯;以及一澆鑄固化步驟:將該鈦鋁介金屬熔湯進行澆鑄,以固化成一鈦鋁介金屬,其中該鈦鋁介金屬,以原子百分比計算,該鈦鋁介金屬包括下列元素:Al:40~50at%、Cr:1~8at%、Nb:1~8at%、Mo:1~5at%、Mn:1~6at%、Ni+Si+Fe:1~15at%及B:0.05~0.8at%,其餘部分為Ti及不可避免之雜質。 The present invention further provides a manufacturing method of titanium-aluminum intermetallic for improving casting fluidity, which includes the following steps: a smelting step: placing a plurality of smelting raw materials of the titanium-aluminum intermetallic in an induction melting device, and smelting these The raw materials are melted into a titanium-aluminum intermetallic broth with casting fluidity; and a casting solidification step: the titanium-aluminum intermetallic broth is cast to solidify into a titanium-aluminum intermetallic, wherein the titanium-aluminum intermetallic is expressed in atomic percentages By calculation, the titanium aluminum intermetallic includes the following elements: Al: 40~50at%, Cr: 1~8at%, Nb: 1~8at%, Mo: 1~5at%, Mn: 1~6at%, Ni+Si+ Fe: 1~15at% and B: 0.05~0.8at%, the rest is Ti and unavoidable impurities.
本發明之鈦鋁介金屬具有較佳的鑄造流動性,亦即具有較佳的鑄造性。 The titanium-aluminum intermetallic of the present invention has better casting fluidity, that is, better castability.
1:製造設備 1: Manufacturing equipment
11:封閉腔體 11: Closed cavity
12:感應熔煉裝置 12: Induction melting device
121:水冷式坩堝單元 121: Water-cooled crucible unit
122:感應線圈單元 122: induction coil unit
13:水冷式模具 13: Water-cooled mold
14:真空裝置 14: Vacuum device
15:氮氣供應源 15: Nitrogen supply source
16:管路單元 16: pipeline unit
17:量尺 17: Measuring Ruler
20:鈦鋁介金屬熔湯 20: Titanium-aluminum intermetallic molten soup
20’:鈦鋁介金屬 20’: Titanium-aluminum intermetallic
S1:步驟 S1: Step
S2:步驟 S2: Step
圖1為本發明之一實施例之用以改善鑄造流動性之鈦鋁介金屬的 製造方法之流程圖。 Figure 1 is an embodiment of the invention for improving the casting fluidity of titanium aluminum intermetallic Flow chart of manufacturing method.
圖2為本發明之一實施例之鈦鋁介金屬的製造設備之剖面示意圖。 Fig. 2 is a schematic cross-sectional view of a manufacturing equipment of titanium-aluminum intermetallic metal according to an embodiment of the present invention.
圖3a為本發明之鑄造流動性實驗之模具之立體示意圖。 Figure 3a is a three-dimensional schematic diagram of the mold for the casting fluidity experiment of the present invention.
圖3b為本發明之鑄造流動性實驗之操作示意圖。 Figure 3b is a schematic diagram of the operation of the casting fluidity experiment of the present invention.
圖4為本發明之鈦鋁介金屬熔湯澆鑄後之樣貌示意圖,其顯示量測鈦鋁介金屬的螺旋流道長度。 Fig. 4 is a schematic diagram of the appearance after casting of the titanium-aluminum intermetallic molten bath of the present invention, which shows the measurement of the length of the spiral flow channel of the titanium-aluminum intermetallic.
為讓本發明之上述目的、特徵和特點能更明顯易懂,茲配合圖式將本發明相關實施例詳細說明如下。 In order to make the above objectives, features and characteristics of the present invention more obvious and understandable, the relevant embodiments of the present invention will be described in detail as follows in conjunction with the drawings.
圖1為本發明之一實施例之用以改善鑄造流動性之鈦鋁介金屬的製造方法之流程圖。本發明之鈦鋁介金屬的製造方法主要包括下列步驟:(1)熔煉步驟S1:將鈦鋁介金屬之多個熔煉原料放置在一感應熔煉設備內,將該些熔煉原料熔融成一具有鑄造流動性的鈦鋁介金屬熔湯;以及(2)澆鑄固化步驟S2:將該鈦鋁介金屬熔湯進行澆鑄,以固化成一鈦鋁介金屬。 FIG. 1 is a flow chart of a method of manufacturing a titanium-aluminum intermetallic for improving casting fluidity according to an embodiment of the present invention. The manufacturing method of the titanium-aluminum intermetallic of the present invention mainly includes the following steps: (1) Melting step S1: placing a plurality of smelting raw materials of the titanium-aluminum intermetallic in an induction melting device, and melting the smelting raw materials into a casting flow And (2) Casting and solidifying step S2: casting the titanium-aluminum-metallic broth to solidify into a titanium-aluminum-metallic broth.
圖2為本發明之一實施例之鈦鋁介金屬的製造設備之剖面示意圖。該鈦鋁介金屬的製造設備1包括一封閉腔體11、一感應熔煉裝置12、一水冷式模具13、一真空裝置14及一保護氣體供應源15。該感應熔煉裝置12設置於該封閉腔體11內。該感應熔煉裝置12包括一水冷式坩堝單元121及一感應線圈單元122。該水冷式坩堝單元121用以容置多個熔煉原料。該感應線圈單元122環繞該水冷式坩堝單元121,用以感應加熱該些熔煉原料成鈦鋁介金屬熔湯20。該水冷式模具13設置於該封閉腔體11內,用以容置澆鑄後之鈦鋁介金屬熔湯20。該真空裝置14藉由管路單元16連通該封閉腔體11,用以對該封閉腔體11抽真空。該真空裝置14可為真空泵。該保護氣體供應源15藉由該管路單元16連通該封閉腔體11,用以供應保護氣體至該
封閉腔體11。
2 is a schematic cross-sectional view of a manufacturing equipment of titanium aluminum dielectric metal according to an embodiment of the present invention. The titanium-aluminum
舉例,本發明之熔煉步驟S1是指在抽真空後,將含鈦(Ti)、鋁(Al)、鉻(Cr)、鈮(Nb)、鉬(Mo)、錳(Mn)、鎳(Ni)、矽(Si)、鐵(Fe)及硼(B)等的熔煉材料置入感應熔煉裝置12進行真空熔煉,使該些熔煉材料熔融混合成具有特定配比之鈦鋁介金屬熔湯20。例如,真空度:10-2~10-4torr,保護氣體:0.3~0.7Mpa(例如氬氣或氦氣)。含Ti、Al、Cr、Nb、Mo、Mn、Ni、Si、Fe及B等的該些熔煉材料包括鋁鈮合金、二硼化鈦及含Cr、Mo、Mn、Ni、Si及Fe的純元素。在熔煉步驟S1之熔煉溫度範圍約為1550~1650℃,進行5~10分鐘的持溫熔煉。
For example, the smelting step S1 of the present invention refers to removing titanium (Ti), aluminum (Al), chromium (Cr), niobium (Nb), molybdenum (Mo), manganese (Mn), nickel (Ni) after vacuuming ), silicon (Si), iron (Fe), boron (B) and other smelting materials are placed in the
再者,本發明之澆鑄固化步驟S2將該鈦鋁介金屬熔湯20進行澆鑄(澆鑄溫度約為:1550~1650℃),例如澆鑄至該水冷式模具13,經過冷卻後,可固化成一種鈦鋁介金屬20’,藉此使固化後之鈦鋁介金屬20,以原子百分比計算,包括下列元素:Al:40~50at%、Cr:1~8at%、Nb:1~8at%、Mo:1~5at%、Mn:1~6at%、Ni+Si+Fe:1~15at%及B:0.05~0.8at%,其餘部分為Ti及不可避免之雜質。詳言之,當前述熔煉材料加入感應熔煉裝置12以形成熔融合金後,接著便取樣測量該感應熔煉裝置12中熔融合金之原子成分比例,以確定該熔融混合之鈦鋁介金屬熔湯20之組成原子百分比維持在,Al:40~50at%、Cr:1~8at%、Nb:1~8at%、Mo:1~5at%、Mn:1~6at%、Ni+Si+Fe:1~15at%及B:0.05~0.8at%,其餘部分為Ti及不可避免之雜質。在Ni+Si+Fe:1~15at%的條件下,Ni8at%,Si8at%,Fe8at%。
Furthermore, in the casting and solidification step S2 of the present invention, the titanium-aluminum intermetallic
鉻(Cr)、鐵(Fe)、錳(Mn)及鎳(Ni)的加入可降低鈦鋁介金屬之合金液相線溫度,提高鈦鋁介金屬熔湯的過熱度,減緩凝固時間,同時明顯提高固液相線區間,增加合金流動性。矽(Si)一方面能夠提高合金的抗氧化性,可減少高溫鈦鋁介金屬熔湯表面形成氧化膜,從而降低鈦鋁介金屬熔湯表面張力,提高合 金流動性;另一方面可以減少鈦鋁介金屬熔湯與殼模之間的反應程度,提高邊界金屬熔湯的流動速度。硼(B)有晶粒細化之功效有益於提升流動性,因細小的晶粒會阻礙粗大樹枝晶的生長,從而使臨界固相率提高,因此會增加流動時間與充填長度。 The addition of chromium (Cr), iron (Fe), manganese (Mn) and nickel (Ni) can lower the alloy liquidus temperature of the titanium-aluminum intermetallic, increase the superheat of the titanium-aluminum intermetallic melt, and slow down the solidification time. Significantly increase the solid-liquid line interval and increase the alloy fluidity. Silicon (Si) on the one hand can improve the oxidation resistance of the alloy, and can reduce the formation of oxide film on the surface of the high-temperature titanium-aluminum-metal molten bath, thereby reducing the surface tension of the titanium-aluminum-metal molten bath and improving the alloy. Gold fluidity; on the other hand, it can reduce the degree of reaction between the titanium-aluminum intermetallic broth and the shell mold, and increase the flow rate of the boundary metal broth. Boron (B) has the effect of grain refinement and is beneficial to improve fluidity, because fine grains will hinder the growth of coarse dendrites, thereby increasing the critical solid phase ratio, thus increasing the flow time and filling length.
由於鈦鋁介金屬之鑄造流動性相當複雜,因此本發明之澆鑄固化步驟S2必須設計一種實驗方法才能收集有效之數據收集。請參考圖3a,其顯示鑄造流動性實驗之模具。請參考圖3b,其顯示鑄造流動性實驗之示意圖。在本實施例中,該模具30為陶瓷模具,並將鈦鋁介金屬熔湯20澆鑄至該模具30內,採澆鑄後之鈦鋁介金屬20’的螺旋流道進行鑄造流動性實驗,流道尺寸設計為長×寬(8mm×8mm),以螺旋流道長度可判斷其鑄造流動性的程度,並得知提升之效果,並與商用鈦鋁介金屬材料(TiAl4822)進行比較。請參考圖4,其顯示鈦鋁介金屬熔湯澆鑄後之樣貌,並使用量尺17量測澆鑄後之鈦鋁介金屬20’的螺旋流道長度,用以將該鑄造流動性的程度數值化。本發明之實施例1~4與比較例11之鈦鋁介金屬的成分比例及螺旋流道長度的差異,如下表1所示:
由上述表1可知,實施例2之鈦鋁介金屬的螺旋流 道長度73.8cm為最長,代表實施例2之鈦鋁介金屬之鑄造流動性最好,亦即鑄造性最佳。 It can be seen from Table 1 above that the spiral flow of the titanium-aluminum intermetallic in Example 2 The channel length of 73.8 cm is the longest, which represents that the casting fluidity of the titanium-aluminum intermetallic in Example 2 is the best, that is, the casting performance is the best.
綜上所述,本發明之鈦鋁介金屬,以原子百分比計算,該鈦鋁介金屬包括下列元素:Al:40~50at%、Cr:1~8at%、Nb:1~8at%、Mo:1~5at%、Mn:1~6at%、Ni+Si+Fe:1~15at%及B:0.05~0.8at%,其餘部分為Ti及不可避免之雜質所構成,具有較佳的鑄造流動性,亦即具有較佳的鑄造性。 In summary, the titanium-aluminum intermetallic of the present invention, calculated in atomic percentage, includes the following elements: Al: 40-50at%, Cr: 1-8at%, Nb: 1-8at%, Mo: 1~5at%, Mn: 1~6at%, Ni+Si+Fe: 1~15at% and B: 0.05~0.8at%, the rest is composed of Ti and inevitable impurities, which has better casting fluidity , That is, it has better castability.
綜上所述,乃僅記載本發明為呈現解決問題所採用的技術手段之較佳實施方式或實施例而已,並非用來限定本發明專利實施之範圍。即凡與本發明專利申請範圍文義相符,或依本發明專利範圍所做的均等變化與修飾,皆為本發明專利範圍所涵蓋。 To sum up, it only describes the preferred embodiments or examples of the technical means adopted by the present invention to solve the problems, and is not used to limit the scope of the patent implementation of the present invention. That is to say, all changes and modifications that are consistent with the scope of the patent application of the present invention or made in accordance with the scope of the patent of the present invention are all covered by the scope of the patent of the present invention.
S1:步驟 S1: Step
S2:步驟 S2: Step
Claims (10)
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
TW109138781A TWI744075B (en) | 2020-11-06 | 2020-11-06 | Titanium-aluminum intermetallic and method for manufacturing the same for improving casting fluidity |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
TW109138781A TWI744075B (en) | 2020-11-06 | 2020-11-06 | Titanium-aluminum intermetallic and method for manufacturing the same for improving casting fluidity |
Publications (2)
Publication Number | Publication Date |
---|---|
TWI744075B true TWI744075B (en) | 2021-10-21 |
TW202219288A TW202219288A (en) | 2022-05-16 |
Family
ID=80782741
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
TW109138781A TWI744075B (en) | 2020-11-06 | 2020-11-06 | Titanium-aluminum intermetallic and method for manufacturing the same for improving casting fluidity |
Country Status (1)
Country | Link |
---|---|
TW (1) | TWI744075B (en) |
Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN107034384A (en) * | 2017-04-26 | 2017-08-11 | 东北大学 | A kind of excellent low cost titanium acieral of thermal deformation working ability |
-
2020
- 2020-11-06 TW TW109138781A patent/TWI744075B/en active
Patent Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN107034384A (en) * | 2017-04-26 | 2017-08-11 | 东北大学 | A kind of excellent low cost titanium acieral of thermal deformation working ability |
Also Published As
Publication number | Publication date |
---|---|
TW202219288A (en) | 2022-05-16 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
AU2020101822A4 (en) | Mn-Cu-based damping alloy powder for use in selective laser melting process and preparation method thereof | |
CN105861886B (en) | A kind of alusil alloy and preparation method thereof for compressor of air conditioner cylinder body | |
TWI613296B (en) | Aluminum alloy powder and manufacturing method of aluminum alloy object | |
US10018203B2 (en) | Al alloy cast impeller for compressor and process for producing same | |
JP2010053743A (en) | Die-cast compressor impeller | |
JP4266196B2 (en) | Nickel-base superalloy with excellent strength, corrosion resistance and oxidation resistance | |
CN112522564A (en) | TiB2Particle reinforced nickel-based casting high-temperature alloy and preparation method thereof | |
TWI744075B (en) | Titanium-aluminum intermetallic and method for manufacturing the same for improving casting fluidity | |
JP6428116B2 (en) | Die for forging and manufacturing method thereof | |
JP5201775B2 (en) | High temperature alloy | |
US20190368006A1 (en) | PREFORM AND METHOD FOR PRODUCING TiAl-BASED TURBINE WHEEL | |
US11708626B2 (en) | Titanium-aluminum intermetallic and manufacturing method thereof for improving casting fluidity | |
CN108165780B (en) | Preparation method of Ni-Cr-Al-Fe high-temperature alloy | |
CN114737072B (en) | K417G nickel-based high-temperature alloy refining preparation and forming method | |
CN109439955A (en) | A method of high strength & high electric-conduction ultrafine wire alloy material is prepared using directional solidification | |
TWI807483B (en) | Heat treatment method and device for titanium-aluminum intermetallic | |
US11807911B2 (en) | Heat treatment method for titanium-aluminum intermetallic and heat treatment device therefor | |
Ma et al. | Possibility of As-Cast Applications on β-Type Titanium Alloys Proposed in the Newly Expanded Area of Bot-Mdt Diagram | |
JP2008196367A (en) | Cast impeller for compressor and its manufacturing method | |
KR20180081313A (en) | Directional solidification ni base superalloy and manufacturing method therefor | |
CN104328311B (en) | There is niobium casting TiAl alloy in the thermal crack resistant type of peritectic freezing feature | |
Li et al. | Effects of AlCrFeNiTi HEA Addition on Microstructure and Mechanical Properties of Hypereutectic Al–20Si Alloy | |
JP5415655B1 (en) | Compressor impeller made of Al alloy casting and manufacturing method thereof | |
CN116516212A (en) | Preparation method of high-temperature high-strength high-Nb-TiAl alloy | |
Dong et al. | Effect of casting process and Zr, V addition on microstructure and mechanical properties of Al–12Si-4.5 Cu–2Ni alloy |