CN104837766A - 金刚石多晶体及其制造方法和工具 - Google Patents

金刚石多晶体及其制造方法和工具 Download PDF

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CN104837766A
CN104837766A CN201380063777.6A CN201380063777A CN104837766A CN 104837766 A CN104837766 A CN 104837766A CN 201380063777 A CN201380063777 A CN 201380063777A CN 104837766 A CN104837766 A CN 104837766A
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polycrystalline diamond
equal
less
coating
raw material
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CN104837766B (zh
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佐藤武
山本佳津子
池田和宽
角谷均
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Sumitomo Electric Industries Ltd
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Sumitomo Electric Industries Ltd
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Abstract

本发明提供一种多晶金刚石体，在涉及滑动的应用中，其比常规的多晶金刚石体寿命更长。本发明还提供制备所述多晶金刚石体的方法和工具。在该多晶金刚石体(2)中，添加有至少一种这样的元素，该元素的硫化物或氯化物的熔点小于或等于1000℃，该多晶金刚石体的平均晶体粒径小于或等于500nm。由此减小了该金刚石的磨损，从而使得在涉及滑动的应用中具有更长的使用寿命。

Description

金刚石多晶体及其制造方法和工具
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，本发明涉及用于利用润滑剂进行塑性加工的耐磨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，金刚石因其具有极高的硬度和优异的耐磨性而被用于以拉模为代表的耐磨部件。
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，当金刚石的摩擦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。据认为这是由于摩擦面的温度高，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，当将金刚石用于耐磨部件时，耐磨部件的寿命较短。
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，其中在发生摩擦时该金刚石多晶体的寿命长于常规金刚石多晶体。
解决问题的方案
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，该元素的硫化物或氯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使用根据本发明的金刚石多晶体。
根据本发明的制造金刚石多晶体的方法包括以下步骤：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，该元素的硫化物或氯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；以及将所述碳材料直接转化为金刚石多晶体。
根据本发明的制造金刚石多晶体的方法包括以下步骤：通过用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，其中所述覆层含有这样的元素，该元素的硫化物或氯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。
本发明的有益效果
根据本发明可以提供一种金刚石多晶体、其制造方法、以及工具，其中在发生摩擦时该金刚石多晶体具有更长的寿命。
附图简要说明
图1为示出了根据本发明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利用润滑剂进行塑性加工的耐磨部件，可使耐磨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，该元素的硫化物或氯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。
在根据本发明的实施方案的金刚石多晶体中，添加有至少一种这样的元素，该元素的硫化物或氯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，可以抑制该金刚石多晶体的磨损，并且当该金刚石多晶体发生摩擦时其能够具有更长的寿命。
上述金刚石多晶体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，并且所述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可析出于作为第一相的所述晶粒的晶界处。此外，上述金刚石多晶体可以包含第二相，所述第二相含有所述元素的单质、碳化物、或氧化物，并且该第二相设置于作为第一相的所述晶粒的晶界处。此外，在所述晶界附近可获得大于或等于90GPa的努氏硬度。这里，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，可以添加大于或等于0.5ppm且小于或等于70ppm的铁。作为上述元素，可以添加大于或等于40ppm且小于或等于80ppm的锶。作为上述元素，可添加总计大于或等于40.5ppm且小于或等于100ppm的铁和锶。
根据本发明的实施方案的工具可以使用根据本发明的实施方案的金刚石多晶体。
根据本发明的实施方案的制造金刚石多晶体的方法包括以下步骤：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，该元素的硫化物或氯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；以及将所述碳材料直接转化为金刚石多晶体。
由此，可以制备如上所述的金刚石多晶体。
上述混合用原料可含有选自由所述元素的单质、碳化物、以及氧化物构成的组中的至少一者。
根据本发明的实施方案的制造金刚石多晶体的方法包含以下步骤：通过用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，其中所述覆层含有这样的元素，该元素的硫化物或氯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，可以制备如上所述的金刚石多晶体。
在制造具有覆层的碳材料的上述步骤中，可以通过溅射法用所述元素包覆所述石墨原料的粉末的表面。在制造具有覆层的碳材料的上述步骤中，所述覆层可以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种者。上述元素可以包括铁和锶中的至少一者。在上述直接转化的步骤中，可以使用如下条件：大于或等于10GPa且小于或等于30GPa的压力，以及大于或等于1500℃且小于或等于3000℃的加热温度。
[本申请的发明的实施方案的详述]
下面，将描述本发明的实施方案。在本发明实施方案的金刚石多晶体中，添加了铁(Fe)作为所述元素，该元素的硫化物的熔点小于或等于1000℃的元素，并且作为第一相的晶粒的平均粒径小于或等于500nm。Fe包含在第二相中，该第二相设置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Fe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。
当添加到上述金刚石多晶体中的Fe(包括其单质、碳化物、和氧化物)暴露在该金刚石多晶体的表面并且因摩擦等受热时，其与含氯润滑剂中所含的氯(Cl)发生反应并生成氯化铁(FeCl3)。由于FeCl3的熔点为302℃，因此当金刚石多晶体被加热到上述沸点以上时，氯化物熔化为液体。由此，当将金刚石多晶体用作工具并与待加工部件间发生摩擦时，FeCl3由于摩擦热而液化，因而金刚石多晶体与被加工部件在其之间的接触面中的至少一部分处相互接触，并且，具有低剪切应力的液化的氯化铁介于其间。由此，上述接触面的摩擦系数降低，因而降低了将金刚石多晶体用于耐磨部件时该金刚石多晶体的磨损量。因此，所述金刚石多晶体和配备有所述金刚石多晶体的工具可以具有更长的寿命。
上述金刚石多晶体中的Fe浓度大于或等于0.5ppm且小于或等于70ppm。由此，即使在第二相的附近，该金刚石多晶体也可具有高硬度(大于或等于90GPa的努氏硬度)，并且可以实现由Fe带来的上述效果。需要注意的是，在Fe浓度低于0.5ppm的金刚石多晶体中，由Fe带来的上述效果不明显。另一方面，在Fe浓度大于70ppm的金刚石多晶体中，第二相附近的努氏硬度小于90GPa，因而其硬度不足以用于工具。
从后面的实施例可以证实，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Fe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20ppm的Fe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Fe浓度为大于或等于0.5ppm且小于或等于70ppm。
根据本实施方案的工具配备有本实施方案的金刚石多晶体，并且用于利用润滑剂进行塑性加工。该工具的例子可包括拉模、划线工具(scribing tool)等。如上所述，当本实施方案的金刚石多晶体用作(例如)耐磨工具，并与待加工部件和含氯润滑剂一同发生摩擦时，通过摩擦热而产生了液化的FeCl3。由此，当本实施方案的工具与待加工部件发生摩擦时，该工具与被加工部件在其之间的接触面中的至少一部分处相互接触，并且，具有低剪切应力的液化的氯化铁介于其间。由此，上述接触面的摩擦系数降低，因而可以降低金刚石多晶体的磨损量。因此，根据本实施方案的工具在进行使用润滑剂的塑性加工时可以具有较长的寿命。
下面将参照图1说明制造本实施方案的金刚石多晶体的方法。制造本实施方案的金刚石多晶体的方法包括以下步骤：通过将石墨原料与Fe金属粉末混合从而制备混合物(S01)，其中Fe金属粉末作为其硫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从而制备碳材料(S02)；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(S03)。
首先，在步骤(S01)中，准备并混合石墨原料与Fe金属粉末从而制备混合物。作为石墨原料，准备杂质浓度极低的石墨原料。所准备的Fe金属粉末的量为这样的量：通过该量使得Fe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Fe浓度。具体而言，为了制备含30ppm的Fe的金刚石多晶体，这样准备石墨原料与Fe金属粉末，以使得混合物中的浓度设为30ppm。
接下来，在步骤(S02)中，通过利用行星式球磨机将在前一步骤(S01)中制备的石墨原料和Fe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Fe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Fe偏析为单质、碳化物或氧化物。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Fe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Fe而具有优异的耐磨性。
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。
在本发明实施方案的金刚石多晶体中，虽然形成了第二相并且Fe构成了该第二相，但本发明并不限于此。Fe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Fe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Fe的单质、碳化物和氧化物所构成的组中的至少一者可析出于第一相的晶界处。此外，选自由Fe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Fe颗粒可在第一相的晶界内结晶为Fe的碳化物，其他Fe颗粒可结晶为Fe的单质。此外，在该情况中，金刚石多晶体因Fe而具有改善耐磨性的效果。
此外，虽然将Fe添加到本实施方案的金刚石多晶体中，但本发明并不限于此。可以将任何元素添加到本发明的金刚石多晶体中，只要其硫化物或氯化物的熔点小于或等于1000℃即可。
这里，采用硫化物或氯化物的熔点小于或等于1000℃的元素的原因是，当金刚石多晶体用于耐磨部件时，由于摩擦热，使金刚石多晶体与待加工部件之间的接触部的温度达到约1000℃。即，由于金刚石多晶体含有这样的元素，该元素的硫化物或氯化物的熔点小于或等于1000℃的元素，因此其能够在上述接触部的界面处产生液态的硫化物或氯化物，并降低摩擦系数。
当如上所述使用含氯润滑剂进行塑性加工时，金刚石多晶体可含有任何这样的元素，该元素的氯化物的熔点小于或等于1000℃。另一方面，当使用含硫润滑剂进行塑性加工时，金刚石多晶体可含有任何这样的元素，该元素的硫化物的熔点小于或等于1000℃。在这种情况下，金刚石多晶体与被加工部件在其之间的接触面中的至少一部分处相互接触，并且，具有低剪切应力的液化的硫化物介于其间。由此，可以降低该接触面的摩擦系数。
需要注意的是，本发明的金刚石多晶体只要含有这样的元素即可，该元素的硫化物或氯化物的熔点低于将金刚石多晶体用作工具时，因其与被加工部件的摩擦所预计达到的温度。换言之，可以将任意元素添加到金刚石多晶体中，只要该元素的硫化物或氯化物的熔点小于发生摩擦时该金刚石多晶体所达到的温度即可。例如，在应用于所达到的温度为约500℃的加工应用的金刚石多晶体中，添加了这样的元素，该元素的硫化物或氯化物的熔点小于或等于500℃。作为其硫化物或氯化物具有100℃至500℃的低熔点的元素，可以采用(例如)选自银(Ag)、铜(Cu)等中的至少一者来代替铁。另外，作为其硫化物或氯化物具有500℃至1000℃的高熔点的元素，可以采用(例如)选自锶(Sr)、钠(Na)等中的一者。
另外，可以添加多种元素，这些元素的硫化物或氯化物的熔点不同。由此，即使在使用上述金刚石多晶体的工具与待加工部件之间产生的摩擦热有所变化的情况下，也能抑制金刚石多晶体的磨损，从而实现更长的寿命。这里，需要注意的是，通过多种元素的组合而形成的化合物可能会析出于金刚石多晶体的晶界处，其中所述多种元素的硫化物或氯化物的熔点不同。在这种情况下，由于这些元素的硫化物或氯化物以及该化合物具有不同的熔点，因此当金刚石多晶体发生摩擦时，也有可能无法充分产生液态硫化物或氯化物。在添加其硫化物或氯化物的熔点不同的多种元素的情况下，优选考虑如上情况来选择所添加的元素、添加量等。
上述金刚石多晶体可含有这样的元素，该元素的硫化物或氯化物的熔点小于或等于1000℃。由此，无论塑性加工过程中使用的润滑剂是含氯润滑剂还是含硫润滑剂，均能够提供耐磨性改善的金刚石多晶体和工具。
需要注意的是，在上述情况下，当添加到金刚石多晶体中的元素是Sr时，优选将其浓度设为大于或等于40ppm且小于或等于80ppm。当添加元素是Na时，优选将其浓度设为大于或等于0.1ppm且小于或等于50ppm。此外，当添加Fe和Sr时，优选将其总浓度设为大于或等于40.5ppm且小于或等于100ppm。此外，当添加元素为Ag或Cu时，优选将其浓度设为大于或等于0.1ppm且小于或等于100ppm。如果各元素的浓度低于下限值，则不能充分实现抑制金刚石多晶体的磨损并延长其寿命的效果。另外，如果各元素的浓度高于上限值，则各元素偏析的区域附近的硬度低于90GPa，由此该金刚石多晶体不适合用于要求高硬度的工具。
在本实施方案的金刚石多晶体制造方法的步骤(S01)中，虽然将Fe金属粉末用作了添加元素，但本发明并不限于此。可通过混合石墨原料和混合用原料来制备混合物，所述混合用原料含有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。另外，以这种方式，可以得到这样的金刚石多晶体，该金刚石多晶体具有与本实施方案的金刚石多晶体相同的特性。
此外，在根据本实施方案的金刚石多晶体制造方法的步骤(S02)中，尽管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，在根据本实施方案的金刚石多晶体制造方法中，尽管通过粉碎并混合Fe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，通过用Fe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)。例如，可通过溅射法、蒸发法等用Fe包覆石墨原料的粉末的表面。此外，通过这种方式，可制造根据本发明的金刚石多晶体。
下面，将描述本发明的实施例。
实施例
通过如下方法制造根据实施例1和2的金刚石多晶体。首先，通过混合Fe粉末单质和石墨原料从而制备混合物，并在15GPa的压力和2300℃的温度下将该混合物转化为金刚石多晶体，从而制造实施例1的金刚石多晶体。实施例1的金刚石多晶体中添加有20ppm的Fe，并且平均粒径为200nm。
通过混合Na粉末单质和石墨原料从而制备混合物，并在15GPa的压力和2300℃的温度下将该混合物转化为金刚石多晶体，从而制造实施例2的金刚石多晶体。实施例2的金刚石多晶体中添加有0.3ppm的Na，并且平均粒径为200nm。
通过在15GPa的压力和2300℃的温度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，从而制造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。
通过以下技术来测量如上所述得到的实施例1、2和比较例的金刚石多晶体的耐磨性。
当将实施例1、2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、2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。此时，作为润滑剂，使用了含氯润滑剂。
测量的结果能够证实：与使用了比较例的金刚石多晶体2的模具相比，使用了实施例1、2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、2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硫化物或氯化物的熔点小于或等于1000℃。
虽然上面已经描述了本发明的实施方案和实施例，但上述实施方案和实施例还可以以各种方式进行变型。此外，本发明的范围并不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确定，并旨在包含等同于权利要求范围和含义内的所有变型。
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使用润滑剂进行塑性加工的耐磨部件。
附图标记列表
1：模具；2：金刚石多晶体；3：孔。

Claims (14)

1.一种金刚石多晶体，其中添加有至少一种这样的元素，该元素的硫化物或氯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，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，并且
包含第二相，该第二相设置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0.5ppm小于或等于70ppm的铁。
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40ppm小于或等于80ppm的锶。
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，添加有总计大于或等于40.5ppm小于或等于100ppm的铁和锶。
7.一种工具，其使用了根据权利要求1至6中任意一项所述的金刚石多晶体。
8.一种制造金刚石多晶体的方法，包括以下步骤：
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，该元素的硫化物或氯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
将所述碳材料直接转化为金刚石多晶体。
9.根据权利要求8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。
10.一种制造金刚石多晶体的方法，包括以下步骤：
通过用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，其中所述覆层含有这样的元素，该元素的硫化物或氯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。
11.根据权利要求10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。
12.根据权利要求10或11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。
13.根据权利要求8至12中任意一项所述的制造金刚石多晶体的方法，其中所述元素包括铁和锶中的至少一者。
14.根据权利要求8至13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，使用了如下条件：压力大于或等于10GPa小于或等于30GPa，并且加热温度大于或等于1500℃小于或等于3000℃。
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