CN104837765A - 金刚石多晶体及其制造方法、以及工具 - Google Patents
金刚石多晶体及其制造方法、以及工具 Download PDFInfo
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- CN104837765A CN104837765A CN201380063645.3A CN201380063645A CN104837765A CN 104837765 A CN104837765 A CN 104837765A CN 201380063645 A CN201380063645 A CN 201380063645A CN 104837765 A CN104837765 A CN 104837765A
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- polycrystalline diamond
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- carbon material
- oxide compound
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- C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
- C04B35/52—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on carbon, e.g. graphite
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- B01J3/062—Processes using ultra-high pressure, e.g. for the formation of diamonds; Apparatus therefor, e.g. moulds or dies characterised by the composition of the materials to be processed
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- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C3/00—Profiling tools for metal drawing; Combinations of dies and mandrels
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Abstract
本发明提供了一种金刚石多晶体,在涉及滑动的应用中,与常规金刚石多晶体相比其寿命更长。本发明还提供制造所述金刚石多晶体的方法和工具。在该金刚石多晶体(2)中,添加有至少一种这样的元素,该元素的氧化物的熔点小于或等于1000℃,并且平均晶粒直径小于或等于500nm。由此减少了金刚石的磨损,结果在涉及滑动的应用中具有更长的使用寿命。
Description
技术领域
本发明涉及金刚石多晶体、其制造方法、以及工具。具体而言,本发明涉及用于滑动部件的金刚石多晶体、其制造方法、以及由该金刚石多晶体制成的工具。
背景技术
一直以来,由于金刚石具有极高的硬度和优异的耐磨性,因此其已被用于以拉模为代表的滑动部件。
例如,日本专利公开No.09-124394披露了一种耐磨部件,其中通过CVD法用金刚石膜包覆充当基体的物质。
此外,日本专利公开No.2009-174039披露了一种滑动部件,其中通过等离子化学气相沉积法用金刚石状碳膜包覆基材的表面。
引用列表
专利文献
专利文献1:日本专利公开No.09-124394
专利文献2:日本专利公开No.2009-174039
发明内容
技术问题
然而,当金刚石的滑动面的温度极高时会迅速磨损。例如,当由金刚石制成的拉模的拉丝速度增加时,金刚石的磨损迅速进行。据认为这是由于滑动面的温度高,金刚石会与氧或被加工部件发生反应,从而发生所谓的反应磨损。因此,当将金刚石用于滑动部件时,滑动部件的寿命较短。
本发明旨在解决前述问题。本发明的主要目的是提供一种金刚石多晶体、其制造方法、以及工具,其中在滑动时该金刚石多晶体的寿命长于常规金刚石多晶体。
解决问题的手段
在根据本发明的金刚石多晶体中,添加有至少一种这样的元素,该元素的氧化物的熔点小于或等于1000℃,并且晶粒的平均粒径小于或等于500nm。
根据本发明的工具可以使用根据本发明的金刚石多晶体。
在本发明的一个方面中,制造金刚石多晶体的方法包括如下步骤:通过将石墨原料与混合用原料混合以制备混合物,其中该混合用原料含有这样的元素,该元素的氧化物的熔点小于或等于1000℃;通过粉碎并混合所述混合物以制备碳材料;以及将所述碳材料直接转化为金刚石多晶体。
在本发明的另一方面中,制造金刚石多晶体的方法包括如下步骤:通过用这样的覆层包覆石墨原料的粉末表面,以制备具有覆层的碳材料,其中该覆层含有这样的元素,该元素的氧化物的熔点小于或等于1000℃;以及将所述具有覆层的碳材料直接转化为金刚石多晶体。
发明的有益效果
根据本发明,可提供金刚石多晶体、其制造方法、以及使用该金刚石多晶体的工具,其中该金刚石多晶体在滑动时具有更长的寿命。
附图简要说明
图1为示出了根据本发明实施方案的制造金刚石多晶体的方法的流程图。
图2为示出了根据本发明实施方案的制造金刚石多晶体的方法的变型的流程图。
图3为示出了本发明实施例1至3中的模具的图。
具体实施方式
[本申请的发明的实施方案的描述]
本发明的发明人为了解决上述问题进行了深入研究,结果发现通过将这样的金刚石多晶体用于滑动部件,可使滑动部件具有更长的寿命,其中在该金刚石多晶体中,添加有至少一种这样的元素,该元素的氧化物的熔点小于或等于1000℃,并且该金刚石多晶体中晶粒的平均粒径小于或等于500nm。
(1)在根据本发明实施方案的金刚石多晶体中,添加有至少一种这样的元素,该元素的氧化物的熔点小于或等于1000℃,并且晶粒的平均粒径小于或等于500nm。
由此,可抑制金刚石的磨损,并且金刚石多晶体在滑动时可具有更长的寿命。
(2)上述金刚石多晶体可包括第二相,该第二相包含选自由所述元素的单质、碳化物和氧化物所构成的组中的至少一者,并且该第二相排布于作为第一相的所述晶粒的晶界处。在晶界附近可获得大于或等于90GPa的努氏硬度。此处,表述“晶界附近”是指第一相中这样的区域:当在该区域中通过利用微型努氏压头在0.5N的测试负荷下进行努氏硬度测量时,努氏压痕不会越过晶界并且不会抵达(例如)作为第二相的另一相邻晶粒。需要注意的是,在该情况中,可在第一相的任何区域中获得大于或等于90GPa的努氏硬度。作为上述元素,可添加大于或等于0.05ppm且小于或等于50ppm的铬。作为上述元素,可添加大于或等于20ppm且小于或等于60ppm的钼。作为上述元素,可添加大于或等于0.05ppm且小于或等于80ppm的锰。作为上述元素,可添加总计大于或等于0.1ppm且小于或等于100ppm的铬和锰。作为上述元素,可添加总计大于或等于0.05ppm且小于或等于200ppm的硼。
根据本发明实施方案的工具可使用根据本发明实施方案的金刚石多晶体。
在本发明实施方案的一个方面中,制造金刚石多晶体的方法包括如下步骤:通过将石墨原料与混合用原料混合以制备混合物,其中该混合用原料含有这样的元素,该元素的氧化物的熔点小于或等于1000℃;通过粉碎并混合所述混合物以制备碳材料;以及将所述碳材料直接转化为金刚石多晶体。
由此,可制备上述金刚石多晶体。
在制备混合物的上述步骤中,可使作为上述混合用原料的、选自由所述元素的单质、碳化物和氧化物构成的组中的至少一者与石墨原料混合。
在本发明实施方案的另一方面中,制造金刚石多晶体的方法包括如下步骤:通过用这样的覆层包覆石墨原料的粉末表面以制备具有覆层的碳材料,其中该覆层含有这样的元素,该元素的氧化物的熔点小于或等于1000℃;以及将所述具有覆层的碳材料直接转化为金刚石多晶体。
由此,可制造上述金刚石多晶体。
在制备具有覆层的碳材料的上述步骤中,可通过溅射法用所述元素包覆所述石墨原料的粉末的表面。在制备具有覆层的碳材料的上述步骤中,覆层可包含选自由所述元素的单质、碳化物和氧化物构成的组中的至少一者。作为上述元素,可选自由硼、砷、铬、钼和锰所构成的组中的至少一者。在直接转化的上述步骤中,通过在这样的条件下烧结所述碳材料从而将所述碳材料直接转化为金刚石,该条件为压力大于或等于10GPa且小于或等于30GPa、并且温度大于或等于1500℃且小于或等于3000℃。
[本申请的发明的实施方案的详述]
下面,将对本发明的实施方案进行说明。在本实施方案的金刚石多晶体中,添加了铬(Cr)作为元素,该元素的氧化物的熔点小于或等于1000℃,并且作为第一相的晶粒的平均粒径小于或等于500nm。Cr包含在第二相中,该第二相排布于作为第一相的晶粒的晶界处。此处,第一相由基本上不包含粘合剂、烧结助剂、催化剂等的金刚石单相制成。另一方面,第二相基本上不包含粘合剂、烧结助剂和催化剂等,并且由Cr的单质、碳化物或氧化物制成。
即,本实施方案的金刚石多晶体具有空隙极少的紧密堆积的结晶结构,其中,由金刚石单相制成、并且平均粒径小于或等于500nm的晶粒彼此间牢固地直接结合在一起。在上述晶粒的晶界处形成了含有所述添加元素的第二相。因此,上述金刚石多晶体即使在高温下仍具有优异的硬度性能。
当上述金刚石多晶体中的形成第二相的Cr因滑动等而暴露于金刚石多晶体的表面并被加热时,Cr会与周围的氧发生反应并生成氧化铬(CrO3)。由于CrO3的熔点为197℃,因此当金刚石多晶体被加热至该熔点以上时,该氧化物会熔融为液体。因此,当将该金刚石多晶体用作工具并在被加工部件上滑动时,因滑动而产生的摩擦热会使氧化铬液化,因而金刚石多晶体与被加工部件在它们之间的接触面的至少一部分处相互接触,并且,液化的氧化铬介于其间。由此,上述接触面的摩擦系数下降,从而减少了金刚石多晶体的磨损量。因而可实现更长的滑动寿命。
上述金刚石多晶体中的Cr浓度为大于或等于0.05ppm且小于或等于50ppm。由此,即使在晶界附近,金刚石多晶体仍能具有高硬度(努氏硬度大于或等于90GPa),并且还可实现由Cr带来的上述效果。需要注意的是,在Cr浓度小于0.05ppm的金刚石多晶体中,并未显著表现出由Cr带来的上述效果。另一方面,对于Cr浓度大于50ppm的金刚石多晶体,其在晶界附近处的努氏硬度小于90GPa,因而其硬度不足以用作工具。
从下文中所描述的实施例可证实,对于其中由金刚石单相制成的晶粒的平均粒径为200nm并且其中添加有0.2ppm的Cr作为添加元素的金刚石多晶体、以及其中平均粒径为200nm并且其中添加有30ppm的Cr的金刚石多晶体,它们作为拉模时的寿命比常规拉模更长。然而,据认为,通过采用这样的金刚石多晶体也可获得相同的效果:在该金刚石多晶体中,由金刚石单相制成的晶粒的平均粒径为小于或等于500nm、并且Cr浓度为大于或等于0.05ppm且小于或等于50ppm。
如上所述,本实施方案的金刚石多晶体可用作工具。本实施方案的金刚石多晶体只要含有这样的元素即可,该元素的氧化物的熔点低于将金刚石多晶体用作工具时由其与被加工部件的摩擦所预计达到的温度。如上所述,当本实施方案的金刚石多晶体(例如)在被加工部件上滑动时,因滑动而产生的摩擦热生成了液化的氧化铬。因此,本实施方案的工具在金刚石多晶体和被加工部件之间的接触面的至少一部分处与被加工部件接触,并且,液化的氧化铬介于其间。由此,上述接触面的摩擦系数降低,因而可减少金刚石多晶体的磨损量。因此,当进行塑性加工时,根据本实施方案的工具可具有更长的寿命。
接下来,将参照图1对根据本实施方案的制造金刚石多晶体的方法进行说明。根据本实施方案的制造金刚石多晶体的方法包括如下步骤:通过将石墨原料与(例如)Cr金属粉末混合以制备混合物(S01),其中Cr为其氧化物的熔点小于或等于1000℃的元素;通过粉碎并混合所述混合物以制备碳材料(S02);以及在高温和高压下将所述碳材料直接转化为金刚石多晶体(S03)。
首先,在步骤(S01)中,准备石墨原料和Cr金属粉末并混合,从而制备混合物。作为石墨原料,准备杂质浓度极低的石墨原料。所准备的Cr金属粉末的量为这样的量:通过该量使得Cr金属粉末在混合物中的浓度被设定为金刚石多晶体中的预定Cr浓度。具体而言,为了制备含有30ppm的Cr的金刚石多晶体,这样准备石墨原料和Cr金属粉末,使得混合物中的浓度设为30ppm。
接下来,在步骤(S02)中,通过利用(例如)行星式球磨机将在前一步骤(S01)中制备的石墨原料和Cr金属粉末的混合物粉碎并混合,从而制备粉末状的碳材料。
接下来,在步骤(S03)中,利用超高压高温发生器将在前一步骤(S02)中制备的碳材料直接转化为金刚石多晶体。在压力大于或等于10GPa且温度大于或等于1500℃的条件下进行向金刚石多晶体的转化。由此,可获得添加有30ppm的Cr的金刚石多晶体。此处,该金刚石多晶体包括作为由金刚石单相制成的晶粒的第一相,该金刚石单相基本上不包含粘合剂、烧结助剂、催化剂等,并且该晶粒的平均粒径小于或等于500nm。金刚石多晶体还包括第二相,其中Cr偏析为选自由单质、碳化物和氧化物所构成的组中的至少一者。第二相形成于作为第一相的晶粒的晶界处。需要注意的是,在该步骤(S03)中,压力和温度的上限值可设定为使金刚石热动力学稳定的任何值,并且压力和温度的上限值实际上取决于所用的超高压高温发生器。例如,工业上稳定制造所允许的上限值为:压力约30GPa,温度约3000℃。
由下文所述的实施例可证实,在步骤(S03)中,在压力为约15GPa且温度为约2300℃的条件下获得的金刚石多晶体作为拉模较常规拉模具有更长的寿命。然而,据认为,即使在压力大于或等于约10GPa且温度大于或等于约1500℃的条件下仍可获得具有相同性质的金刚石多晶体。
如上所述,根据本实施方案的金刚石多晶体包括:作为由金刚石单相制成的晶粒的第一相,该晶粒的平均粒径为小于或等于500nm;以及形成于所述晶粒的晶界处的第二相,在该第二相中Cr偏析。因此,根据本实施方案的金刚石多晶体除了具有金刚石的高硬度性质外,还因含有Cr而具有优异的耐磨性。
另外,在根据本实施方案的金刚石多晶体中,尽管由金刚石单相形成的晶粒的平均粒径小于或等于500nm,但是该平均粒径优选小于或等于300nm。由此,金刚石多晶体可具有空隙极少的、更为紧密堆积的结晶结构,并且可具有更优异的硬度性质。
在本实施方案的金刚石多晶体中,尽管Cr作为单质构成了第二相,但是本发明并不局限于此。Cr可作为选自由单质、碳化物和氧化物构成的组中的至少一者而构成第二相,只要Cr在由金刚石单相形成的晶粒的晶界处偏析为第二相即可。具体而言,选自由Cr的单质、碳化物和氧化物所构成的组中的至少一者可沉积于第一相的晶界处。此外,选自由Cr的单质、碳化物和氧化物所构成的组中的至少一者可在第一相的晶界处结晶。在本实施方案的制造金刚石多晶体的方法中,取决于步骤(S03)中的温度,例如,在碳材料内石墨附近的Cr颗粒可在第一相的晶界内结晶为Cr的碳化物,其他Cr颗粒可在第一相的晶界内结晶为Cr的单质。此外,在该情况中,金刚石多晶体因Cr而具有改善耐磨性的效果。需要注意的是,第一相的晶界处优选具有较少的空隙。因此,当含有Cr的晶粒构成第二相时,优选该晶粒具有较小的粒径。
此外,尽管将Cr添加至本实施方案的金刚石多晶体中,但是本发明并不局限于此。添加至本发明的金刚石多晶体中的元素为其氧化物的熔点小于或等于1000℃的元素。这是因为,当将金刚石多晶体用于滑动部件时,与被加工部件之间的摩擦热会使金刚石多晶体的温度达到约1000℃,因此,这时金刚石多晶体会在其接触部分的界面处生成液态氧化物,从而降低摩擦系数。因此,本发明的金刚石多晶体只要含有这样的元素即可:该元素的氧化物的熔点低于将金刚石多晶体用作工具时由其与被加工部件的摩擦所预计达到的温度。换言之,可向金刚石多晶体中加入任何元素,只要其氧化物的熔点小于或等于金刚石多晶体滑动时所达到的温度即可。例如,向用于温度会达到约500℃的加工用途的金刚石多晶体中加入这样的元素,该元素的氧化物的熔点小于或等于500℃。作为其氧化物具有100℃至500℃的低熔点的元素,例如,可采用选自磷(P)、砷(As)等的组中的至少一者。此外,作为其氧化物具有500℃至1000℃的高熔点的元素,例如,可采用选自锰(Mn)、钼(Mo)、铋(Bi)等的组中的一者。通过按照本实施方案的制造金刚石多晶体的方法添加上述元素,该添加元素在金刚石多晶体的晶界处发生偏析。此处,如上所述,所添加的元素可以这样存在:作为选自由单质、碳化物和氧化物构成的组中的一者在晶界处形成第二相,或者作为单质或者选自上述组中的两者或更多者的混合物而沉积于晶界处。
此外,所添加的元素可通过取代碳原子而包含于作为第一相的金刚石晶体中。例如,可使用硼(B)作为添加元素,并且通过在步骤(S01)中利用B粉末单质来制备混合物并将该混合物转化,从而制备金刚石多晶体。在该情况中,所添加的B中的一部分通过取代碳原子而存在于第一相中,而所添加的B的其余部分在晶界处以单质和碳化物的形式构成了第二相。需要注意的是,如果B的添加量较小,则B可能不会沉积于晶界处,而可能仅包含于第一相中。此外在该情况中,暴露于金刚石多晶体表面处的硼在高温下被氧化,从而生成氧化硼,并且当温度达到高于氧化硼熔点的温度时,氧化硼被液化。因此,可获得滑动时具有更长寿命的金刚石多晶体。
另外,在这种情况中,可添加多种元素,这些元素的氧化物具有不同的熔点。因此,即使在利用上述金刚石多晶体的工具与被加工部件之间所产生的摩擦热有变化时,也可抑制金刚石多晶体的磨损,从而实现更长的寿命。此处,需要注意的是,通过组合多种元素(该多种元素的氧化物具有不同的熔点)而形成的化合物可能在金刚石多晶体中的晶界处偏析。在这种情况中,由于这些元素的氧化物和化合物具有不同的熔点,因此当金刚石多晶体产生摩擦时,也可能无法充分形成液态氧化物。在所添加的多种元素的氧化物具有不同熔点的情况中,优选的是,考虑到如上情况来选择所添加的元素、添加量等。
需要注意的是,如上所述,当添加至金刚石多晶体中的元素为Mo时,优选将其浓度设定为大于或等于20ppm且小于或等于60ppm。当添加元素为Mn时,优选将其浓度设定为大于或等于0.05ppm且小于或等于80ppm。此外,当添加元素为Cr和Mn时,优选将其总浓度设定为大于或等于0.1ppm且小于或等于100ppm。另外,当添加Cr和Mn时,优选将其总浓度设定为大于或等于0.1ppm且小于或等于100ppm。如果各元素的浓度均小于其下限值,则难以显著实现抑制金刚石多晶体的磨损并延长其寿命的效果。此外,如果各元素的浓度均大于其上限值,则各元素发生偏析的区域附近的硬度小于90GPa,由此该金刚石多晶体不适用于要求高硬度的工具。
尽管在根据本实施方案的制造金刚石多晶体的方法中在步骤(S01)中使用了Cr金属粉末作为添加元素,但是本发明并不局限于此。可通过混合石墨原料和混合用原料来制备混合物,其中该混合用原料包含选自由添加元素的单质、碳化物和氧化物构成的组中的至少一者。此外,通过这种方式,可以获得具有与本实施方案的金刚石多晶体性能相同的金刚石多晶体。
此外,尽管在根据本实施方案的制造金刚石多晶体的方法的步骤(S02)中,通过利用行星式球磨机将所述混合物粉碎并混合从而制备碳材料,但是本发明不局限于此。可通过能够以高均匀性粉碎并混合该混合物的任何方法来制备碳材料。
另外,尽管在根据本实施方案的制造金刚石多晶体的方法中,通过粉碎并混合Cr金属粉末和石墨原料来制备碳材料,但是本发明不局限于此。参见图2,例如,可通过用Cr包覆石墨原料的粉末的表面以制备具有覆层的碳材料(S11),并可在高温高压条件下将该具有覆层的碳材料直接转化为金刚石多晶体(S12)。作为用Cr包覆石墨原料的粉末的表面的方法,例如,可使用溅射法。此外,通过这种方式,也可制造根据本发明的金刚石多晶体。
下面将对本发明的实施例进行说明。
实施例
通过下述方法来制备根据实施例1至3的金刚石多晶体。首先,通过混合Cr粉末单质和石墨原料以制备混合物,并在压力为15GPa且温度为2300℃的条件下将该混合物转化为金刚石多晶体,从而制备实施例1的金刚石多晶体。实施例1的金刚石多晶体中添加有0.2ppm的Cr,并且平均粒径为200nm。
通过将Cr粉末单质和石墨原料混合以制备混合物,并在压力为15GPa且温度为2300℃的条件下将该混合物转化为金刚石多晶体,从而制备实施例2的金刚石多晶体。实施例2的金刚石多晶体中添加有15ppm的Cr,并且平均粒径为200nm。
通过将Mo粉末单质和石墨原料混合以制备混合物,并在压力为15GPa且温度为2300℃的条件下将该混合物转化为金刚石多晶体,从而制备实施例3的金刚石多晶体。实施例3的金刚石多晶体中添加有10ppm的Mo,并且平均粒径为200nm。
通过在压力为15GPa且温度为2300℃的条件下将石墨原料转化为金刚石多晶体,而没有进行添加元素的添加,从而制备比较例的金刚石多晶体。比较例的金刚石多晶体的平均粒径为200nm。
通过下述技术来测量按如上方式获得的实施例1至3和比较例的金刚石多晶体的耐磨性。
当将实施例1至3和比较例的金刚石多晶体用于模具以对SUS316进行拉伸(拉丝)时,评价其耐磨性。参见图3,使用具有孔径为φ30μm的孔3(其中,实施例1至3和比较例的各金刚石多晶体2被施加于加工表面)的模具1,以1000m/分钟的拉丝速度对SUS316进行拉伸,对模具1中的孔直径扩大至φ30.5μm时所花费的拉伸时间进行测量。这时,基于对紧邻各金刚石多晶体2的表面处所产生的温度的计算结果,据认为各金刚石多晶体2在拉伸过程中的温度达到了约200℃至400℃。
测量的结果能够证实:与使用了比较例的金刚石多晶体的模具相比,使用了实施例1至3的金刚石多晶体的模具的上述拉伸时间要长四倍。即,能够证实实施例1至3的金刚石多晶体具有更长的寿命,这是因为它们所包含的元素的氧化物的熔点小于或等于1000℃。
尽管上面对本发明的实施方案和实施例进行了说明,但是上述实施方案和实施例还可以进行各种形式的变型。此外,本发明的范围并不局限于上述实施方案和实施例。本发明的范围由权利要求的范围限定,并且旨在包括在等同于权利要求范围的范围和含义内的任何变型。
工业实用性
本发明的金刚石多晶体、其制造方法、以及工具特别有利地应用于耐磨部件。
附图标记列表
1:模具;2:金刚石多晶体;3:孔。
Claims (16)
1.一种金刚石多晶体,其中添加有至少一种这样的元素,该元素的氧化物的熔点小于或等于1000℃,并且
其中晶粒的平均粒径小于或等于500nm。
2.根据权利要求1所述的金刚石多晶体,包括第二相,该第二相包含选自由所述元素的单质、碳化物和氧化物构成的组中的至少一者,并且该第二相排布于作为第一相的所述晶粒的晶界处。
3.根据权利要求1或2所述的金刚石多晶体,所述晶界附近的努氏硬度大于或等于90GPa。
4.根据权利要求1至3中任意一项所述的金刚石多晶体,其中,作为所述元素,添加有大于或等于0.05ppm且小于或等于50ppm的铬。
5.根据权利要求1至3中任意一项所述的金刚石多晶体,其中,作为所述元素,添加有大于或等于20ppm且小于或等于60ppm的钼。
6.根据权利要求1至3中任意一项所述的金刚石多晶体,其中,作为所述元素,添加有大于或等于0.05ppm且小于或等于80ppm的锰。
7.根据权利要求1至3中任意一项所述的金刚石多晶体,其中,作为所述元素,添加有总计大于或等于0.1ppm且小于或等于100ppm的铬和锰。
8.根据权利要求1至3中任意一项所述的金刚石多晶体,其中,作为所述元素,添加有大于或等于0.05ppm且小于或等于200ppm的硼。
9.一种工具,其使用了权利要求1至8中任意一项所述的金刚石多晶体。
10.一种制造金刚石多晶体的方法,包括如下步骤:
通过将石墨原料与混合用原料混合从而制备混合物,其中该混合用原料含有这样的元素,该元素的氧化物的熔点小于或等于1000℃;
通过粉碎并混合所述混合物从而制备碳材料;以及
在高温和高压条件下将所述碳材料直接转化为金刚石多晶体。
11.根据权利要求10所述的制造金刚石多晶体的方法,其中所述混合用原料含有选自由所述元素的单质、碳化物和氧化物构成的组中的至少一者。
12.一种制造金刚石多晶体的方法,包括如下步骤:
通过用这样的覆层包覆石墨原料的粉末的表面从而制备具有覆层的碳材料,其中该覆层含有这样的元素,该元素的氧化物的熔点小于或等于1000℃;以及
将所述具有覆层的碳材料直接转化为金刚石多晶体。
13.根据权利要求12所述的制造金刚石多晶体的方法,其中,在制备所述具有覆层的碳材料的所述步骤中,通过溅射法用所述元素包覆所述石墨原料的粉末的表面。
14.根据权利要求12或13所述的制造金刚石多晶体的方法,其中,在制备所述具有覆层的碳材料的所述步骤中,所述覆层含有选自由所述元素的单质、碳化物和氧化物构成的组中的至少一者。
15.根据权利要求10至14中任意一项所述的制造金刚石多晶体的方法,其中所述元素为选自由硼、砷、铬、钼和锰构成的组中的至少一者。
16.根据权利要求10至15中任意一项所述的制造金刚石多晶体的方法,其中,在所述直接转化的步骤中,通过在这样的条件下烧结所述碳材料从而将所述碳材料直接转化为金刚石,该条件为压力大于或等于10GPa且小于或等于30GPa、并且温度大于或等于1500℃且小于或等于3000℃。
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CN109661568A (zh) * | 2017-08-10 | 2019-04-19 | 住友电气工业株式会社 | 多晶金刚石制成的压头及使用压头评价开裂引发载荷的方法和装置 |
CN109661568B (zh) * | 2017-08-10 | 2022-12-23 | 住友电气工业株式会社 | 多晶金刚石制成的压头及使用压头评价开裂引发载荷的方法和装置 |
CN109663543A (zh) * | 2018-12-19 | 2019-04-23 | 郑州中南杰特超硬材料有限公司 | 一种直接转化合成硼皮氮芯多晶金刚石制备方法 |
CN109663543B (zh) * | 2018-12-19 | 2023-02-24 | 郑州中南杰特超硬材料有限公司 | 一种直接转化合成硼皮氮芯多晶金刚石制备方法 |
CN111943676A (zh) * | 2020-08-10 | 2020-11-17 | 四川大学 | 一种高冲击强度的金刚石多相材料及其制备方法 |
CN111943676B (zh) * | 2020-08-10 | 2021-09-21 | 四川大学 | 一种高冲击强度的金刚石多相材料及其制备方法 |
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US9487447B2 (en) | 2016-11-08 |
EP2930145B1 (en) | 2024-03-06 |
JP6056431B2 (ja) | 2017-01-11 |
EP2930145A1 (en) | 2015-10-14 |
WO2014088069A1 (ja) | 2014-06-12 |
US20150307404A1 (en) | 2015-10-29 |
JP2014114170A (ja) | 2014-06-26 |
EP2930145A4 (en) | 2016-09-28 |
CN104837765B (zh) | 2018-01-23 |
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