CN114072247A - 用于快速凝固加工的钛合金 - Google Patents
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- 238000007712 rapid solidification Methods 0.000 title description 10
- 229910001069 Ti alloy Inorganic materials 0.000 title description 4
- 239000000843 powder Substances 0.000 claims abstract description 36
- 239000000463 material Substances 0.000 claims abstract description 16
- 229910052751 metal Inorganic materials 0.000 claims abstract description 16
- 239000002184 metal Substances 0.000 claims abstract description 16
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- 238000000034 method Methods 0.000 claims description 11
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 6
- 229910052719 titanium Inorganic materials 0.000 claims description 5
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 4
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 4
- 229910052760 oxygen Inorganic materials 0.000 claims description 4
- 239000001301 oxygen Substances 0.000 claims description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 3
- 229910052799 carbon Inorganic materials 0.000 claims description 3
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- 239000000758 substrate Substances 0.000 claims description 2
- 238000002844 melting Methods 0.000 abstract description 5
- 230000008018 melting Effects 0.000 abstract description 5
- 229910045601 alloy Inorganic materials 0.000 description 12
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- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 5
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- 238000004458 analytical method Methods 0.000 description 2
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- 238000007711 solidification Methods 0.000 description 2
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- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 description 1
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Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/20—Direct sintering or melting
- B22F10/25—Direct deposition of metal particles, e.g. direct metal deposition [DMD] or laser engineered net shaping [LENS]
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/045—Alloys based on refractory metals
- C22C1/0458—Alloys based on titanium, zirconium or hafnium
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2301/00—Metallic composition of the powder or its coating
- B22F2301/20—Refractory metals
- B22F2301/205—Titanium, zirconium or hafnium
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2303/00—Functional details of metal or compound in the powder or product
- B22F2303/01—Main component
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- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y10/00—Processes of additive manufacturing
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y70/00—Materials specially adapted for additive manufacturing
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y80/00—Products made by additive manufacturing
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Abstract
本发明涉及一种用于生产部件的增材制造方法，包括以下步骤：(a)提供并熔化金属基粉末，(b)将熔化的颗粒相互融合并与它们的基材融合，从而形成融合的材料，(c)冷却，从而使融合的材料凝固，其特征在于，该金属基粉末是Ti基粉末，其至少包括Ta、Fe和i)Sn和/或ii)Nb和Zr。
Description
金属熔体的快速凝固(ΔT≈10至1010K/s)发生在许多技术工艺中，如粉末雾化、焊接、增材制造(AM)、铸造、电弧或等离子体熔化等。梯度导致非平衡相、偏析效应和残余应力，这限制了可加工合金的选择。因此，本发明的目的是公开两种合金体系，它们令人惊讶地显示出出色的快速凝固行为。
在某些应用中，需要细粒的粉末(<1mm)。在其他应用中，需要颗粒状物质(包含尺寸≥1mm的颗粒)。这甚至可能是块状物质。在本说明书的意义上，这些都是粉末。
发明人发现在快速凝固加工性方面显示出最佳性能的金属体系是钛(Ti)+钽(Ta)+铁(Fe)+铌(Nb)+锆(Zr)和Ti+Ta+铁+锡(Sn)。
在下文中简写为TTFNZ和TIFS：
TTFNZ仅可选地包含Sn。
TTFNZ和TTFS的热力学平衡显示在图1、1b和2、2b中。在快速凝固过程(类似于3D打印)后，TTFNZ和TIFS的α/β微观结构和相组成显示在图3、3b和4、4b中。在电弧熔化条件后，TTFNZ和TTFS的β主导的微观结构显示在图5和图6中。
TTFNZ的热力学平衡显示在图1、1b中。在快速凝固(非平衡)和/或最后伴随着热处理以达到接近平衡的微观结构后，针对不同的条件，合金的α/β微观结构用电子背散射探测器(EBSD)分析得到确认。由这些过程产生的不同的微观结构在图2、2b中显示，其中，热处理实现更接近热力学计算的微观结构。
在所调查的工艺窗口中，这种合金显示出与增材制造工艺的高度兼容性，突出表现为加工后没有裂纹。
TTFS的模拟热力学平衡相图显示在图2、2b中。以1K的间隔大小进行模拟。合金在TS＝1922K(基体形成温度)时处于液态，在TS＝1821K时转变为100％相摩尔分数的固态立方体BCC_B2相。这产生约为TLS＝101K的平衡凝固间隔。冷却至1027K后，六方HCP相成核(β-α转变温度)并且被稳定至300K的模拟温度，达到92.88％的相摩尔分数。在这个温度，剩下的相是斜方μ相(Fe7Ta6)，其相摩尔分数为4.3％，以及具有Ta的溶解态的有序的金属间化合物FeTi(BCC_B2#2，立方B2型)。金属间相，如μ相，或次级相，如HCP_A3(α相)的析出引起了材料电阻的增加；这产生了对激光辐射更高的吸收，这可以使基于激光的制造工艺的生产成本降低。
在快速凝固(非平衡)和/或最后伴随着热处理以达到接近平衡的微观结构后，针对不同的条件，合金的α/β微观结构用电子背散射探测器(EBSD)分析得到确认。图6显示了这些过程产生的不同的微观结构，其中，热处理实现了更接近热力学计算的微观结构。
在所研究的加工窗口中，这种合金显示出与增材制造工艺的高兼容性，突出表现为加工后没有裂纹。
根据本发明的另一个方面，由于其高比强度>200kN·m/kg，该新型材料在航空航天、汽车、工具或医疗方面的应用是有意义的。
根据本发明的另一个方面，由于其低密度、高韧性、优良的腐蚀性能和对热裂纹或冷裂纹的抵抗力，这些新型材料对航空航天、汽车、工具或医疗应用很有意义。
金属体系TTFNZ和TTFS特别适用于医疗应用。最常见的植入材料(Ti64、CoCr、316L)[1]具有相对较高的耐腐蚀性，但在人体体液中，它们会暴露在溶解氧、氯化物和蛋白质的非常具有侵蚀性的环境中，其促进Al-、Co-、Cr-、Ni-、V-离子释放到人体内。如果超过痕量，溶解的离子会扰乱细胞的新陈代谢并且导致致命的肿瘤疾病。Ti、Ta、Nb、Zr和它们的合金在耐腐蚀性和生物相容性方面达到了最佳性能。目前用于医疗应用的合金的另一个关键参数是植入材料和硬组织之间的弹性特性不匹配。在这个问题上，所提出的金属体系TTFNZ和TTFS显示出优于既定的ISO[1]和ASTM标准合金的生物相容性。特别是由于生物相容的合金元素和相对较低的弹性模量(E<100GPa，优选<120Gpa)，与既定的ISO[1]和ASTM标准化合金相比，所提出的金属体系TTFNZ在临床使用中应该是优选的。特别是由于生物相容的合金元素和相对较低的弹性模量(E<115GPa，优选<120GPa)，与既定的ISO[1]和ASTM标准化合金相比，所提出的金属体系TTFS在临床使用中应是优选的。
此外，TTFNZ和TTFS的普通AM快速凝固加工可以使组织工程的开放式多孔、仿骨的晶格结构(支架)成为可能，这将允许骨细胞的氧合和营养，实现骨结合和牢固的植入物固定。
根据本发明的另一个方面，关于TTFS，可以考虑在所有现有的钛合金中加入锡(Sn；优选是0.01-10wt.％)，以改善普通增材(AM)的加工性能，特别是焊接性或打印性(AM)。因为Sn可以降低高表面张力和高熔体粘度，这可能会在快速凝固过程中造成球化效应。特别是Sn同时可以增加对激光辐射的吸收，这可以使钛合金的加工更具成本效益。
在这种情况下，Sn可以作为元素粉末添加到预合金化的粉末混合物中，或者Sn可以直接被合金化到预合金化的粉末中。
本说明书是以粉末为重点撰写的。然而，本领域的技术人员了解到，有一些增材制造方法不是基于粉末，而是基于金属丝或例如液体聚合物中的金属粉末混合物。本说明书中介绍的材料也可用于此类方法，这也是本发明的一个方面。
根据本发明的另一个方面，可以考虑在TTFNZ和/或TTFS中加入氧O，和/或碳C，和/或氮，以产生一种坚硬、耐磨的材料。
在本发明中，要求保护一种用于生产部件的增材制造方法，包括以下步骤：
(a)提供并熔化金属基粉末，
(b)将熔化的颗粒相互融合并与它们的基材融合，从而形成融合的材料，
(c)使所述融合的材料冷却且进而凝固，
其特征在于，该金属基粉末是Ti基粉末，其至少包含Ta、Fe和i)Sn和/或ii)Nb和Zr。
优选地，该方法的特征在于，所述Ti基粉末还包括Si。
优选地，该方法的特征在于，所述Ti基粉末包括C和/或N，和/或O。
在本发明中，要求保护一种用于增材制造的Ti基粉末，其特征在于，该粉末包括：
-Ta，在0.01wt％和15wt％的范围内，优选在3wt％和10wt％的范围内，最优选地包含6wt％，和
-Nb，在0.01wt％和25wt％的范围内，优选在4wt％和12wt％的范围内，最优选地包含8wt％，
-Fe，在0.01wt％和15wt％的范围内，优选在2wt％和6wt％的范围内，最优选地包含4wt％，
-Zr，在0.01wt％和25wt％的范围内，优选在3wt％和9wt％的范围内，最优选地包含6wt％。
在本发明中，要求保护一种用于增材制造的Ti基粉末，其特征在于，该粉末包括：
-Ta，在0.01wt％和20wt％的范围内，优选在3wt％和10wt％的范围内，最优选包含7wt％，和
-Fe，在0.01wt％和15wt％的范围内，优选在2wt％和10wt％的范围内，最优选包含5wt％，
-Sn，在0.01wt％和10wt％的范围内，优选在0.1wt％和9wt％的范围内，最优选包含3wt％，
-Si，在0.001wt％和3wt％的范围内。
优选地，该Ti基粉末的特征在于，该粉末包括：
-氧，优选在0.001wt％和0.3wt％的范围内，和/或
-氮，优选在0.001wt％和0.2wt％的范围内，和/或
-碳，优选在0.001wt％和0.9wt％的范围内。
对于上述的一些Ti基粉末，与仅由Ti作为金属元素组成的Ti基粉末的凝固相比，添加到Ti中的金属引起了融合材料粉末的更快速的凝固。在其中一些情况下，这可以通过与纯Ti相比，融合材料的熔点升高来解释。更高的熔点引起冷却过程中，正在凝固的熔体和周围介质之间的更大的温度梯度，从而引起更快的凝固。在此上下文中，更快意味着凝固至少要快1K/s。
关键文献
[1]ISO 5832,手术用植入物-金属材料
Claims (6)
1.一种用于生产部件的增材制造方法，包括以下步骤：
(a)提供并熔化金属基粉末，
(b)将熔化的颗粒相互融合并与它们的基材融合，从而形成融合的材料，
(c)冷却，从而使所述融合的材料凝固，
其特征在于，所述金属基粉末是Ti基粉末，至少包含Ta、Fe和i)Sn和/或ii)Nb和Zr。
2.根据权利要求1所述的方法，其特征在于，所述Ti基粉末也包含Si。
3.根据前述权利要求中任一项所述的方法，其特征在于，所述Ti基粉末包含C和/或N和/或O。
4.用于增材制造的钛基粉末，其特征在于，该粉末包含：
-Ta，在0.01wt％和15wt％的范围内，优选在3wt％和10wt％的范围内，并且最优选地包含6wt％，和
-Nb，在0.01wt％和25wt％的范围内，优选在4wt％和12wt％的范围内，并且最优选地包含8wt％，
-Fe，在0.01wt％和15wt％的范围内，优选在2wt％和10wt％的范围内，更优选在2wt％和6wt％的范围内，并且最优选地包含约4wt％，
-Zr，在0.01wt％和25wt％的范围内，优选在0.01wt％和15wt％的范围内，优选在2wt％和10wt％的范围内，优选在3wt％和9wt％的范围内，并且最优选地包含约6wt％。
5.一种用于增材制造的钛基粉末，其特征在于，该粉末包含：
-Ta，在0.01wt％和20wt％的范围内，优选在3wt％和10wt％的范围内，并且最优选地包含7wt％，和
-Fe，在0.01wt％和15wt％的范围内，优选在2wt％和10wt％的范围内，并且最优选地包含约5wt％，
-Sn，在0.01wt％和10wt％范围内，优选在0.1wt％和9wt％范围内，并且最优选包含约3wt％，
-Si，在0.001wt％和3wt％的范围内。
6.根据权利要求4或5所述的钛基粉末，其特征在于所述粉末包含：
-氧，优选在0.001wt％和0.3wt％的范围内，和/或
-氮，优选在0.001wt％和0.2wt％的范围内，和/或
-碳，优选在0.001wt％和0.9wt％的范围内。
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| JPH03257130A (ja) * | 1990-03-05 | 1991-11-15 | Daido Steel Co Ltd | Ｔｉ―Ａｌ系耐熱材料 |
| JPH05148567A (ja) * | 1991-11-25 | 1993-06-15 | Nkk Corp | 高密度粉末焼結用チタン合金 |
| CN1659302A (zh) * | 2002-05-30 | 2005-08-24 | 德累斯顿协会莱布尼茨固体材料研究所 | 由钛合金构成的高强度的、可塑变形的成型体 |
| CN105154701A (zh) * | 2015-10-14 | 2015-12-16 | 华中科技大学 | 一种采用选择性激光熔化快速成形技术制备高温钛合金的方法 |
| US20170067136A1 (en) * | 2015-09-04 | 2017-03-09 | King Fahd University Of Petroleum And Minerals | Titanium alloys for biomedical applications and fabrication methods thereof |
| CN108486408A (zh) * | 2018-04-18 | 2018-09-04 | 王甲林 | 一种低弹性模量补牙用β型钛合金及其制造方法 |
| WO2018162919A1 (en) * | 2017-03-10 | 2018-09-13 | Ilika Technologies Limited | Titanium alloys |
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- 2020-03-27 WO PCT/EP2020/058761 patent/WO2020193763A1/en unknown
- 2020-03-27 EP EP20715823.9A patent/EP3946782A1/en active Pending
- 2020-03-27 CN CN202080025876.5A patent/CN114072247B/zh active Active
- 2020-03-27 CA CA3135311A patent/CA3135311A1/en active Pending
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Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03257130A (ja) * | 1990-03-05 | 1991-11-15 | Daido Steel Co Ltd | Ｔｉ―Ａｌ系耐熱材料 |
| JPH05148567A (ja) * | 1991-11-25 | 1993-06-15 | Nkk Corp | 高密度粉末焼結用チタン合金 |
| CN1659302A (zh) * | 2002-05-30 | 2005-08-24 | 德累斯顿协会莱布尼茨固体材料研究所 | 由钛合金构成的高强度的、可塑变形的成型体 |
| US20170067136A1 (en) * | 2015-09-04 | 2017-03-09 | King Fahd University Of Petroleum And Minerals | Titanium alloys for biomedical applications and fabrication methods thereof |
| CN105154701A (zh) * | 2015-10-14 | 2015-12-16 | 华中科技大学 | 一种采用选择性激光熔化快速成形技术制备高温钛合金的方法 |
| WO2018162919A1 (en) * | 2017-03-10 | 2018-09-13 | Ilika Technologies Limited | Titanium alloys |
| CN108486408A (zh) * | 2018-04-18 | 2018-09-04 | 王甲林 | 一种低弹性模量补牙用β型钛合金及其制造方法 |
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| WO2020193763A8 (en) | 2021-10-07 |
| AU2020245766A1 (en) | 2021-10-28 |
| MX2021011859A (es) | 2021-12-10 |
| WO2020193763A1 (en) | 2020-10-01 |
| SG11202110765YA (en) | 2021-10-28 |
| BR112021019396A2 (pt) | 2022-01-18 |
| KR20220016043A (ko) | 2022-02-08 |
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| US20220184704A1 (en) | 2022-06-16 |
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