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["1. 合享下载限制：权利要求： 100条/次； 说明书： 100条/次；有合享裸数据平台；\n2. 合享除了说明书，权利要求，附图，其他字段下载未有太大限制，建议补充智慧芽没有的栏位，参见“合享可导出字段”中红色字体部分。这部分主要涉及引用和法律事件的信息导入，待讨论。"]
["国际专利分类(IPC)、欧洲专利分类号(ECLA)、美国专利分类号(UPC/USPC)、日本的分类法(FI/F-term)、联合专利分类(CPC)等;\n比较通用的是IPC;在欧洲专利局的网站既可以使用IPC，也可以使用ECLA(分类体例与IPC类似，但分类更细、更方便);而在美国专利商标局的网站可以使用UPC/USPC以及CPC，日本的FI/F-term比较复杂"]

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["US7316752B2",null,"2001-06-29","R-T-B-C based rare-earth magnetic powder and bonded magnet","US10/481015","B2","The step of preparing a rapidly solidified alloy by rapidly quenching a melt of an R-T-B-C based rare-earth alloy (where R is at least one of the rare-earth elements including Y, T is a transition metal including iron as its main ingredient, B is boron, and C is carbon) and the step of thermally treating and crystallizing the rapidly solidified alloy are included. The step of thermally treating results in producing a first compound phase with an R2Fe14B type crystal structure and a second compound phase having a diffraction peak at a site with an interplanar spacing d of 0.295 nm to 0.300 nm (i.e., where 2θ=30 degrees). An intensity ratio of the diffraction peak of the second compound phase to that of R2Fe14B type crystals representing a (410) plane is at least 10%. The present invention provides an R-T-B-C based rare-earth alloy magnetic material, including carbon (C) as an indispensable element but exhibiting excellent magnetic properties, and makes it possible to recycle rare-earth magnets.","美国","2008-01-08","2008-01-08","通过快速淬火RTBC基稀土合金的熔体制备快速凝固合金的步骤（其中R是包括Y的稀土元素中的至少一种，T是包含铁作为其主要成分的过渡金属，B优选硼，C为碳，并包括热处理和结晶快速凝固合金的步骤。热处理步骤导致产生具有R2Fe14B型晶体结构的第一化合物相和在晶面间距d为0.295nm至0.300nm的位置处具有衍射峰的第二化合物相（即，其中2θ= 30度） 。第二化合物相的衍射峰与表示（410）面的R2Fe14B型晶体的强度比为至少10％。本发明提供一种R-T-B-C基稀土合金磁性材料，其包含碳（C）作为必不可少的元素，但具有优异的磁性，并且可以回收稀土磁体。","基于R-T-B-C的稀土磁粉和粘结磁铁","授权发明",{"$cut":{"chars":32690,"head":"TECHNICAL FIELD\n\n[0001]The present invention relates to a rare-earth magnetic powder that can be used effectively to make a bonded magnet and to a bonded magnet made of such a magnetic powder. More particularly, the present invention relates to an R-T-B-C based rare-earth magnet in which carbon (C) is substituted for a portion of boron (B).\n\nBACKGROUND ART\n\n[0002]Currently, R-T-B based (where R is at least one of the rare-earth elements including Y, T is a transition metal including iron as its main ingredient, and B is boron) rare-earth magnets are extensively used as high-performance magnets in a broad variety of applications. In order to not just save, or at least use more efficiently, valuable natural resources but also cut down the manufacturing cost of the R-T-B based rare-earth magnets, it is important to make those R-T-B based rare-earth magnets recyclable.\n\n[0003]The grinding sludge and fine powder, which are produced during the manufacturing process of R-T-B based sintered magnets, are oxidizable so easily as to possibly ignite spontaneously within the air atmosphere. Accordingly, the sludge and fine powder are normally oxidized intentionally by incineration or any other suitable process so as to turn into chemically stabilized oxides. If those oxides are subjected to a chemical process such as acid dissolution, the rare-earth components thereof can be separated and extracted.\n\n[0004]Meanwhile, techniques of recycling final R-T-B based magnet products into the R-T-B based material alloy by re-melting or any other process are also under research and development.\n\n[0005]However, if the R-T-B based rare-earth magnets are re-melted, then oxygen can be sufficiently removed from the rare-earth magnets but the carbon content thereof rather increases. Other problems may also be caused by the re-melting technique.\n\n[0006]It has been generally believed that to improve the magnet performance and anticorrosiveness of R-T-B based rare-earth magnets, impurities such as oxygen and carbon should be eliminated from the magnets as much as possible. According to this point of view, the technique of removing those impurities is a key to making the R-T-B based rare-earth magnets recyclable more easily and more effectively.\n\n[0007]However, if a special process is required to remove oxygen and carbon, then the manufacturing cost will rise significantly and cannot be reduced effectively. This constitutes a serious obstacle to recycling the rare-earth magnets successfully.\n\n[0008]In attempting to recycle a rare-earth bonded magnet on the other hand, the bonded magnet may be separated into a magnetic powder and a binder resin, and then only the magnetic powder may be subjected to a recycling process. According to this technique, however, such a resin includes too much carbon component to prevent the carbon in the resin from depositing or sticking onto the magnetic powder. Thus, the magnetic powder collected from the bonded magnet should include a lot of carbon and other impurities. For that reason, the bonded magnets, as well as the rare-earth sintered magnets, also require a special carbon removal process, thus making the rare-earth bonded magnets non-recyclable.\n\n[0009]In order to overcome the problems described above, a primary object of the present invention is to provide an R-T-B-C based rare-earth alloy magnetic material, which includes carbon (C) as an indispensable element but can still exhibit excellent magnetic properties, while making rare-earth magnets recyclable.\n\nDISCLOSURE OF INVENTION\n\n[0010]An R-T-B-C based rare-earth alloy magnetic material according to the present invention (where R is at least one of the rare-earth elements including Y, T is a transition metal including iron as its main ingredient, B is boron, and C is carbon) includes a first compound phase with an R2Fe14B type crystal structure and a second compound phase having a diffraction peak at a site with an interplanar spacing d of 0.295 nm to 0.300 nm. An intensity ratio of the diffraction peak of the second compound phase to that of the first compound pha"}},"技术领域 \n\n [0001] 稀土磁粉技术领域本发明涉及一种可以有效地用于制造粘结磁体的稀土磁粉以及由这种磁粉制成的粘结磁体。 更具体地,本发明涉及基于R-T-B-C的稀土磁体,其中碳(C)代替一部分硼(B)。 \n\n 背景技术 \n\n [0002] 目前,基于RTB的稀土磁体被广泛用作高性能磁体,其中RT是稀土元素,其中R是包括Y的稀土元素中的至少一种,T是以铁为主要成分的过渡金属,B是硼。 广泛的应用。 为了不仅节省或至少更有效地利用宝贵的自然资源,同时降低基于R-T-B的稀土磁体的制造成本,重要的是使那些基于R-T-B的稀土磁体可回收。 \n\n [0003] 在基于R-T-B的烧结磁体的制造过程中产生的研磨污泥和细粉易于氧化,以至于可能在空气中自燃。 因此,污泥和细粉通常通过焚烧或任何其他合适的方法被有意地氧化,从而变成化学稳定的氧化物。 如果对这些氧化物进行诸如酸溶解的化学处理,则可以分离和提取其稀土成分。 \n\n [0004] 同时,也正在研究通过再熔融或任何其他方法将最终的基于R-T-B的磁体产品再循环到基于R-T-B的材料合金中的技术。 \n\n [0005] 然而,如果将基于R-T-B的稀土磁体重新熔化,则可以从稀土磁体中充分除去氧,但是其碳含量反而增加了。 重熔技术也可能引起其他问题。 \n\n [0006] 通常认为,为了提高R-T-B系稀土类磁铁的磁铁性能和耐腐蚀性,应尽可能地从磁铁中除去氧和碳等杂质。 根据这种观点,去除那些杂质的技术是使基于R-T-B的稀土磁体更容易和更有效地回收的关键。 \n\n [0007] 然而,如果需要特殊的工艺来去除氧气和碳,则制造成本将显着增加并且不能有效地降低。 这对成功地回收稀土磁体构成了严重的障碍。 \n\n [0008] 另一方面,在尝试使稀土类粘结磁体回收时,可以将粘结磁体分离成磁粉和粘结剂树脂,然后可以仅对磁粉进行回收处理。 然而,根据该技术,这种树脂包含太多的碳成分,以防止树脂中的碳沉积或粘附在磁性粉末上。 因此,从粘结磁体收集的磁粉应包含许多碳和其他杂质。 因此,粘结磁体以及稀土类烧结磁体也需要特殊的除碳处理,因此稀土粘结磁体不可回收。 \n\n [0009] 为了克服上述问题,本发明的主要目的是提供基于RTBC的稀土合金磁性材料,其包含碳(C)作为必不可少的元素,但是仍然表现出优异的磁性能,同时使其稀有。 磁铁可回收。 \n\n 发明内容 \n\n [0010] 根据本发明的基于RTBC的稀土合金磁性材料(其中R为包括Y的稀土元素中的至少一种,T为以铁为主要成分的过渡金属,B为硼,C为碳 )包括带有R的第一化合物相 2 铁 14 B型晶体结构和第二化合物相,该第二化合物相在晶面间距d为0.295nm至0.300nm的部位处具有衍射峰。 第二化合物相的衍射峰与代表(410)面(并且具有0.214nm的晶面间距)的第一化合物相的衍射峰的强度比为至少10%。 \n\n [0011] 在一个优选的实施方案中,R的摩尔分数为整个磁性材料的25重量%至35重量%,B和C的总摩尔分数为磁性材料的0.9重量%至1.1重量%,并且 磁性材料是T。 \n\n [0012] 在另一个优选的实施方案中,C(碳)的含量与B(硼)和C的总含量之比为0.05至0.75。 \n\n [0013] 第一化合物相优选具有10nm至500nm的平均晶粒尺寸。 \n\n [0014] 在另一个优选的实施方案中,R-T-B-C基稀土合金磁性材料通过以下方法获得:通过快速淬火R-T-B-C基稀土合金的熔体来制备快速凝固的合金; 并对快速凝固的合金进行热处理和结晶。 \n\n [0015] T优选包含Fe作为其主要成分,但是Fe的一部分可以被选自由Co,Ni,Mn,Cr和Al组成的组中的至少一种元素代替。 \n\n [0016] 所述基于R-T-B-C的稀土合金磁性材料可以进一步包括选自Si,P,Cu,Sn,Ti,Zr,V,Nb,Mo和Ga的至少一种元素作为添加剂。 \n\n [0017] 本发明的稀土合金磁性粉末是通过将上述的R-T-B-C系稀土合金磁性材料中的任一种粉碎而得到的。 \n\n [0018] 通过加工上述稀土合金磁性粉末来制造根据本发明的粘结磁体。 \n\n [0019] 通过加工上述稀土合金磁性粉末来制造根据本发明的永磁体。 \n\n [0020] 制造基于RTBC的稀土合金磁性材料的发明方法包括以下步骤:通过快速淬火基于RTBC的稀土合金(其中R为至少一种稀土元素)的熔体来制备快速凝固的合金 包括Y,T是包括铁作为主要成分的过渡金属,B是硼,C是碳。 并对快速凝固的合金进行热处理和结晶。 热处理步骤导致产生具有R的第一化合物相 2 铁 14 B型晶体结构和第二化合物相,该第二化合物相在晶面间距d为0.295nm至0.300nm的部位处具有衍射峰。 第二化合物相的衍射峰与代表(410)面的第一化合物相的衍射峰的强度比为至少10%。 \n\n [0021] 制造基于R-T-B-C的稀土合金磁性材料的另一发明方法包括获得基于R-T-B-C的稀土合金磁性材料的步骤,所述含R-T-B-C的稀土合金磁性材料包括具有R的第一化合物相。 2 铁 14 通过快速淬火基于RTBC的稀土合金的熔体(其中R为至少一种R原子)的B型晶体结构和在平面间距d为0.295 nm至0.300 nm的位置处具有衍射峰的第二化合物相 包括Y的稀土元素,T为以铁为主要成分的过渡金属,B为硼,C为碳。 第二化合物相的衍射峰与代表(410)面的第一化合物相的衍射峰的强度比为至少10%。 \n\n [0022] 粉碎处理步骤优选在热处理步骤之前和/或之后进行。 \n\n [0023] 本发明的粘结磁体的制造方法包括以下步骤:制备通过上述方法之一获得的R-T-B-C基稀土合金磁性材料的粉末; 将粉末和粘合剂材料混合在一起并模制该化合物。 \n\n [0024] 制造基于RTBC的稀土合金磁性材料的另一种发明方法包括以下步骤:制备基于RTBC的稀土快速凝固合金(其中R为包括Y的稀土元素中的至少一种,T为过渡元素 以铁为主要成分,B为硼,C为碳的金属)通过熔融,快速淬火并固化回收后的RTB系稀土类磁铁而使其固化。  R-T-B-C基稀土快速凝固合金的热处理和结晶。 \n\n [0025] 在一个优选的实施方案中,热处理步骤导致产生具有R的第一化合物相。 2 铁 14 B型晶体结构和第二化合物相,该第二化合物相在晶面间距d为0.295nm至0.300nm的部位处具有衍射峰,并且第二化合物相与第一化合物相的衍射峰的强度比表示a。  (410)平面至少为10%。 \n\n [0026] 本发明的粘结磁体的制造方法包括以下步骤:制备通过上述方法之一获得的R-T-B-C基稀土合金磁性材料的粉末; 将粉末和粘合剂材料混合在一起并模制该化合物。 \n\n 附图说明 \n\n [0027] 图。  1( a 图1是示出用于根据本发明的制造R-T-B-C基稀土合金磁性材料的方法中的超快速淬火机的总体构造的截面图。 \n\n [0028] 图。  1( b )以更大的比例显示了机器的一部分,用于快速淬火和固化合金。 \n\n [0029] 图。 图2是示出了待热处理和结晶的母合金E的快速凝固的薄带的XRD图的图,其中横坐标表示衍射角(2θ),纵坐标表示衍射峰强度。 \n\n [0030] 图。 图3是示出待热处理和结晶的母合金G的快速凝固的薄带的XRD图案的图,其中横坐标表示衍射角(2θ),纵坐标表示衍射峰强度。 \n\n [0031] 图。 图4是示出作为样品No.22的经热处理且结晶的合金的XRD图案的图,其中横坐标表示衍射角(2θ),纵坐标表示衍射峰强度。 \n\n [0032] 图。 图5是示出作为样品No.8的经热处理且结晶的合金的XRD图案的图,其中横坐标表示衍射角(2θ),纵坐标表示衍射峰强度。 \n\n [0033] 图。 图6是表示式Nd所示的R-T-B-C系稀土合金磁性材料的磁特性的曲线图。 30.0 铁 69.0 乙 (1.0-X) C X  (并在873 K下热处理300秒)随碳比X的变化而变化,碳比X落在0至0.75的范围内。 \n\n [0034] 图。 图7是类似于图6的曲线图。 图6示出了由式Nd表示的R-T-B-C系稀土合金磁性材料的磁特性。 30.0 铁 59.0 有限公司 10.0 乙 (1.0-X) C X  (并在873 K下热处理300秒)随碳比X的变化而变化,碳比X落在0至0.75的范围内。 \n\n [0035] 图。 图8是表示式Nd所示的R-T-B-C系稀土合金磁性材料的磁特性的曲线图。 30.0 铁 69.0 乙 0.75 C 0.25  热处理温度T在873K〜1,073K(即600℃〜800℃)的范围内变化。 \n\n [0036] 图。 图9是表示以Nd为代表的R-T-B-C系稀土合金磁性材料的峰强度比的图。 30.0 铁 69.0 乙 0.75 C 0.25  或钕 30.0 铁 69.0 乙 0.50 C 0.50  热处理温度T在宽范围内变化。 \n\n 实施本发明的最佳模式 \n\n [0037] 本发明人从各种角度分析了包括碳(C)作为其必不可少的成分的基于R-T-B的稀土磁性材料。 结果,本发明人发现,如果通过快速淬火工艺使满足一定组成范围的熔融合金凝固,然后在适当的温度范围内进行热处理,则不仅R 2 铁 14 制备了具有硬磁特性但还具有未知化合物结晶相的B型化合物,该化合物的结晶峰在晶面间距d为0.295nm至0.300nm(例如,d = 0.298nm)的位置处具有衍射峰。 本发明人从该发现中获得了本发明的基本思想。 \n\n [0038] 但是,如果改变合金中的碳含量,任何其他成分的组成范围或结晶化热处理工艺的条件,则化合物晶相在晶面间距为d的位置具有衍射峰 不再以可检测的水平产生0.295 nm至0.300 nm的α(当CuKα用作X射线源时,约为2θ= 30度)。 为了方便起见,这种化合物结晶相在本文中将被称为“第二化合物相”。 到目前为止,尚未阐明该第二化合物相的晶体结构,但可以认为它在改善磁性方面起着重要作用。 \n\n [0039] 本发明人通过实验发现并确认,如果以合金中的碳量生成第二化合物相,则可以适当调整其他成分的组成范围和结晶化的热处理工艺条件,并且可以确定其强度比。 第二化合物相相对于R的衍射峰 2 铁 14 代表(410)面(且具有0.214nm的晶面间距)的B型化合物相至少为10%,实际上获得了足够好的磁性能。 为了获得更好的磁性能,该峰强度比优选为30%以上,甚至更优选为50%以上。 \n\n [0040] 已经报道了有意添加碳(C)的R-T-B-C基稀土合金磁性材料。 但是,从未观察到具有这种衍射峰的第二化合物相。 认为原因如下。 具体地,所产生的第二化合物相对材料合金的组成或热处理条件敏感。 因此,如果稀土合金磁性材料在正常条件下制成,则不会产生具有这种衍射峰的第二化合物相。 或者即使产生该复合相,其量也将非常小。 \n\n [0041] 根据本发明,通过向材料合金中添加适量的碳以使碳替代合金中的一部分硼来生产第二化合物。 然后,其剩磁等磁性能提高,并且其耐候性提高。 \n\n [0042] 以这种方式,根据本发明,可以将已经作为杂质处理的碳组分作为必不可少的组分引入。 因此,本发明可用于回收基于R-T-B的烧结磁体或基于R-T-B的粘结磁体。 也就是说,可以从使用和收集的R-T-B基烧结或粘结磁体中获得包括碳成分的材料合金,然后将其有效地加工成根据本发明的R-T-B-C基稀土合金磁性材料。 特别地,如上所述,粘结磁体通常使用树脂作为粘结剂将磁性粉末颗粒粘结在一起。 因此,碳基物质经常牢固地粘附在磁体表面上。 然而,甚至这种磁体也可以有效地用作根据本发明的材料。 \n\n [0043] 应当注意,本发明人证实,例如,本发明的磁性材料不仅表现出优异的磁性,而且表现出良好的耐候性。 \n\n [0044] 根据本发明,硼和碳的总量(即,(B + C))优选为0.9重量%至1.1重量%,而碳的比率(即,C /(B + C))优选为0.05。 到0.75。 \n\n [0045] 任选地,可以用选自由Co,Ni,Mn,Cr和Al组成的组中的至少一种元素代替本发明的材料中包括的一部分Fe。 另外,可以向其中添加选自由Si,P,Cu,Sn,Ti,Zr,V,Nb,Mo和Ga组成的组中的至少一种元素。 \n\n [0046] 在下文中,将描述本发明的优选实施例。 \n\n 熔体淬火机 \n\n [0047] 图1中所示的机器包括:  1( a )包括材料合金熔化室 1  和材料合金淬火室 2 ,其中真空或惰性气氛保持在可调压力下。 具体而言,  1( a )示出了机器的整体布置,而图2示出了机器的总体布置。  1( b )以更大的比例显示了机器的一部分。 \n\n [0048] 如图1所示。  1( a ),熔化室 1  包括:熔体坩埚 3  在高温下熔化一种材料 20  已混合以具有所需的磁铁合金成分; 一个水库 4  带吸嘴 5  在底部; 和混合材料给料机 8  将混合材料供应到熔融坩埚中 3  同时保持气密状态。 水库 4  储存熔体 21  在其中填充有材料合金,并设有加热器(未示出),以将从中收集的熔体的温度保持在预定水平。 \n\n [0049] 淬火室 2  包括旋转的冷却辊 7  用于快速淬火和固化熔体 21  通过吸嘴喷出的 5 。 \n\n [0050] 在这台机器中,熔化和淬火室内的气氛和压力 1  和 2  可控制在规定范围内。 为此,大气进气口 1 b , 2 b  和 8 b  和出口 1 a , 2 a  和 8 a  在机器的适当位置提供。 特别是出气口 2 a  连接到泵以控制淬火室中的绝对压力 2  在真空至80 kPa的范围内。 \n\n [0051] 熔体坩埚 3  可以定义所需的倾角以倾倒熔体 21  通过一个漏斗 6  进入水库 4 。 融化 21  在水箱中加热 4  通过加热器(未显示)。 \n\n [0052] 吸嘴 5  水库的 4  位于熔化室和淬火室之间的边界壁上 1  和 2  滴熔 21  从水库 4  到冷却辊的表面 7 ,位于喷嘴下方 5 。 充填喷嘴的孔口直径 5  例如,可以为0.5mm至2.0mm。 如果熔体的粘度 21  高,然后融化 21  不能流过吸嘴 5  容易。 然而,在该实施例中,淬火室中的压力 2  保持低于熔化室中的压力 1 。 因此,在熔化室和骤冷室之间产生了适当的压力差。 1  和 2 和融化 21  可以顺利地装满。 另外,由于本发明的材料合金包括碳,因此熔融合金具有如此低的粘度以至于足以不断滴落。 \n\n [0053] 冷却辊 7  优选由Cu,Fe或包含Cu或Fe的合金制成。 这是因为如果冷却辊由Cu或Fe以外的材料制成,则所得到的快速凝固的合金不能容易地离开冷却辊并且可能缠绕在辊上。 冷却辊 7  可以具有例如300mm至500mm的直径。 冷却辊内部装有水冷却器的水冷却能力 7  根据凝固潜热和每单位时间吸积的熔体体积计算和调整。 \n\n [0054] 图1至图3中所示的机器。  1( a )和 1 ( b )可以在10到20分钟内快速固化10公斤材料合金。 以这种方式获得的快速凝固的合金为合金薄带(或合金带)的形式 22  例如,具有10μm至300μm的厚度和2mm至3mm的宽度。 \n\n 熔融淬火过程 \n\n [0055] 一,融化 21  具有上述组成的材料合金的一部分被制备并存储在储罐中 4  熔化室的 1  如图所示。  1( a )。 在该优选实施例中,通过向其中添加铁碳将碳引入到材料合金中。 材料合金也可以从收集和使用的稀土烧结磁体或粘结磁体中获得。 \n\n [0056] 接下来,融化 21  通过吸嘴滴下 5  放在水冷辊上 7  与冷却辊接触并迅速冷却并固化 7  在低压Ar气氛中。 在这种情况下,优选采用适当的快速凝固技术,其使得冷却速率可精确控制。 在这个实施例中,熔体 21  最好以10的速度冷却 2 °C / s至10 7 °C /秒 \n\n [0057] 融化的一段时间 21  被冷却辊淬火 7  等于合金与旋转冷却辊的外周接触的时间点之间的间隔 7  合金及时离开辊子 7 。 在这段时间里,合金的温度降低到固化。 之后,凝固的合金离开冷却辊 7  并在惰性气氛中旅行。 当薄带合金移动时,合金的热量散发到大气中。 结果,合金的温度进一步下降。 \n\n [0058] 在该优选实施方式中,通过将辊表面速度控制在5m / s至50m / s的范围内,获得了包括非晶相的快速凝固的合金。 原因如下。 具体地,如果辊表面速度小于5m / s,则尺寸过大的结晶相成核并生长并且不能形成所需的微晶结构。 然而,通常难以通过可批量生产的设备实现超过50m / s的辊表面速度。 另外,即使可以实现如此高的辊表面速度,磁性能也不应如此显着地提高。 辊表面速度更优选为20m / s至50m / s。 \n\n [0059] 在本发明中,将熔体快速淬火的技术不限于上述的单辊熔体纺丝法。 其他适用技术的实例包括双辊法,气体雾化法,带铸法和结合使用辊和气体雾化法的快速淬火技术。 \n\n [0060] 根据本发明,材料合金包括碳,因此可以更有效地产生非晶相。 因此,即使冷却速率相对较低,仍可以以高再现性生产包括许多非晶相的快速凝固的合金。 因此,即使通过薄带连铸法也可以得到磁性优异的磁性合金,在上述各种急冷技术中,可以确保大量生产,但是冷却速度较低。 \n\n 热处理 \n\n [0061] 在该优选实施例中,热处理在氩气氛中进行。 优选地,以5℃/ s至200℃/ s的升温速率加热合金,并在550℃至750℃的温度下保持30秒至60秒的时间。 分钟,然后冷却至室温。 该热处理导致R的晶体生长 2 铁 14 B结晶相和第二化合物相处于非晶相。 \n\n [0062] 如果热处理温度低于550℃,则无R 2 铁 14 B型结晶相将成核,矫顽力会明显降低。 另一方面,如果热处理温度超过750℃,则各构成相的晶粒生长过大,因此剩磁B降低。 r  并使退磁曲线的环路矩形度恶化。 由于这些原因,热处理温度优选为550℃至750℃,更优选550℃至700℃。 \n\n [0063] 为了防止合金被氧化,优选在惰性气体(例如,Ar或N)中进行热处理。 2  50 kPa以下的气体。 热处理也可以在0.1kPa以下的真空内进行。 \n\n [0064] 应该注意的是,快速凝固的合金薄带在进行热处理之前可以粗切或粉碎。 \n\n [0065] 在热处理之后,将所得的磁性材料精细地粉碎以获得磁体粉末。 然后,可以通过对该粉末执行已知的处理步骤来由该粉末制造各种类型的粘结磁体。 在制造粘结磁体时,将本发明的磁体粉末与环氧或尼龙树脂粘合剂混合,然后将该化合物成型为期望的形状。 在这种情况下,可以将任何其他类型的磁体粉末(例如,基于Sm-T-N的磁体粉末或硬质铁氧体磁体粉末)与本发明的磁体粉末混合。 \n\n [0066] 使用所得的粘结磁体,可以生产电动机,致动器和其他旋转机械。 \n\n [0067] 如果使用磁体粉末来制造注射成型的粘结磁体,则优选将粉末粉碎至平均粒径为150μm或更小,更优选1μm至100μm。 另一方面,如果使用磁体粉末来制造压缩粘结磁体,则优选将粉末粉碎至300μm或更小的平均粒径,更优选50μm至200μm,甚至更优选50μm至150。 具有双峰尺寸分布的μm。 \n\n 例子 \n\n [0068] 首先,通过感应熔融法制备具有下表1所示的各组成的母合金。  Nd使用纯度为99.5%以上的原料,碳使用碳含量为3.0质量%的铁碳,其他成分分别使用纯度为99.9%以上的原料。 在Ar气氛中,将材料合金在氧化铝坩埚中熔融。 \n\n [0069] \n\n   表格1  重量%  标志 钕 铁 有限公司 B C M1 M2  A 25.0 74.2 0.0 0.40 0.40  B 27.0 72.1 0.0 0.45 0.45  C 27.0 71.8 0.0 0.60 0.60  D 28.0 71.1 0.0 0.55 0.35  E 30.0 69.0 0.0 1.00 0.00  F 30.0 69.0 0.0 0.75 0.25  G 30.0 69.0 0.0 0.50 0.50  H 30.0 69.0 0.0 0.75 0.25  I 30.0 69.0 0.0 0.00 1.00  J 30.0 68.6 0.0 0.75 0.25 铝:0.40  K 30.0 68.2 0.0 0.75 0.25 铝:0.50 铜:0.30  L 30.0 63.5 5.0 0.75 0.25 镓:0.50  M 30.0 63.2 5.0 0.75 0.25 钼:0.80  N 30.0 58.4 10.0 0.50 0.50 铬:0.30 铝:0.30  O 35.0 63.8 0.0 0.60 0.60 \n\n [0070] 未向母合金E中添加碳(C)。在母合金I中,硼(B)完全被碳(C)取代。 母合金A中的Nd含量为25wt%,是表1所示的母合金中最小的。另一方面,母合金O中的Nd含量为35wt%,比其他任何一种都大。 母合金见表1。 \n\n [0071] 这些母合金A至O中的每一种的熔体通过单辊工艺快速冷却并固化,从而获得快速固化的合金薄带。 用于快速淬火过程的冷却辊由Cu制成,并以35 m / s的圆周速度旋转。 将母合金在具有直径为0.7mm的孔的石英管中熔融。 石英管孔口的末端与辊子表面之间的距离(或间隙)定义为0.5 mm。 快速淬火气氛是压力为50kPa的Ar气。 所用的Ar气的压差为50 kPa,足以将熔体充分喷出。 \n\n [0072] 无花果 图2和图3是分别示出快速固化的薄带的XRD图案的图,其在进行热处理和结晶之前用CuKα辐射源测量。 横坐标表示衍射角2θ,纵坐标表示衍射强度。 具体而言, 图2涉及比较例,其中使用了不包含添加剂碳(C)的母合金E,而图3是使用了不添加碳(C)的母合金E的对比例。 图3涉及本发明的示例,其中使用了包括适量碳的母合金G。 \n\n [0073] 从快速淬火工艺获得的每个快速凝固的合金薄带包括许多结晶相,如从图1和2中所示的XRD数据可以看出的。  2和3,矫顽力H  J 100 kA / m或更小。 \n\n [0074] 用玛瑙研钵将这种快速固化的合金细带粉碎至500μm以下的尺寸,然后进行热处理以使其结晶化,以保持在500℃至1000℃的温度。 在Ar气氛中放置30分钟。 用VSM和X射线衍射分析对热处理过的粉末进行磁性能评估。 结果示于下表2: \n\n [0075] \n\n    表2  热处理 磁性 衍射  母亲 温度 物产 周围  没有。 合金 (°C) 溴(T) 立方英尺(kA / m) d = 0.298纳米  1 B 600 0.90 890 ◯  2 D 600 0.88 1140 ◯  3 F 560 0.77> 1200  ⊚  4 F 610 0.78> 1200  ⊚  5 F 650 0.76 1170 ⊚  6 F 700 0.73 1030 ⊚  7 G 570 0.74> 1200  ⊚  8 G 600 0.71> 1200  ⊚  9 H 580 0.74> 1200  ⊚  10 H 620 0.70 1190 ⊚  11 H 700 0.70 1050 ⊚  12 J 570 0.78> 1200  ⊚  13 J 650 0.79> 1200  ⊚  14 K 610 0.79> 1200  ⊚  15 L 610 0.76> 1200  ⊚  16 M 600 0.72> 1200  ⊚  17 N 600 0.70> 1200  ⊚  18 N 700 0.68> 1200  ⊚  19 C 600 0.78 470 Δ  20 A 600 0.67 180 X  21 O 600 0.61> 1200  ⊚  22 E 600 0.73> 1200  X  23 I 600 0.50 150 X  24 G 500 0.42 120 X  25 G 800 0.35 210 Δ \n\n [0076] 表2显示了所用母合金的符号,热处理温度,磁性能(例如剩磁B) r  和矫顽力H  J  )和每个样品在d = 0.298 nm附近(即2θ= 30.0度附近)是否存在衍射峰。 在表2的最右列,双圆圈⊚表示强度为R的80%以上的衍射峰。 2 铁 14 在d = 0.298nm附近(即在2θ= 30.0度附近)观察到代表(410)面(2θ= 42.2度)的B型结晶相。 单圆圈◯表示在d = 0.298nm附近(即在2θ= 30.0度附近)观察到强度为该衍射峰的10%以上(2θ= 42.2度)的衍射峰。 空心三角形Δ表示在d = 0.298nm附近(即,在2θ= 30.0度附近)观察到强度为该衍射峰的5%至10%(2θ= 42.2度)的衍射峰。  。 十字×表示在d = 0.298nm附近未观察到衍射峰。 \n\n [0077] 从表2可以看出,当在d = 0.298nm附近观察到具有足够强度的衍射峰时,获得了优异的磁性能。 另一方面,如果由母合金E的熔体制成完全不添加碳的快速凝固的合金,则基本上不产生第二化合物相,并且即使在d = 0.298nm附近也未观察到其衍射峰。 之后,将合金在600℃加热并结晶。 \n\n [0078] 另外,即使由具有适当组成的母合金G制成快速凝固的合金,在d = 0.298nm附近也未观察到第二化合物相的衍射峰,并且当在室温下进行结晶化热处理时磁性能差。  500℃以下或800℃以上的温度。 \n\n [0079] 无花果 图4和图5是分别示出已经进行了结晶热处理的快速固化的薄带的XRD图的图。 具体而言, 图4涉及作为比较例的22号样品,其中使用了不包含添加剂碳(C)的母合金E,而图4示出了作为比较例的样品E。 图5涉及作为本发明示例的8号样品,其中使用了包括适量碳的母合金G。 \n\n [0080] 从图可以看出,  5,除了代表R的峰 2 铁 14 在具有硬磁性的B型化合物中,在8号样品中在平面间距d为0.295nm至0.300nm(即,d = 0.298nm附近:2θ= 30.0度)的位置清楚地观察到另一个衍射峰。 在图 另一方面,在图4中,在平面间距d = 0.298nm附近(即在2θ= 30.0度附近)没有观察到衍射峰。 \n\n [0081] 在图 如图5所示,第二化合物相的衍射峰的强度比(即,在2θ= 30.0度附近)与R的强度比 2 铁 14 表示(410)面(即2θ= 42.2度)的B型结晶相为100%以上。 \n\n [0082] 接下来,将参照图2至图6描述碳(C)比X与硼(B)和碳(C)之和之间的关系以及磁性能。  6至9。 \n\n [0083] 图。 图6示出了由式Nd表示的R-T-B-C基稀土合金磁性材料的磁性能。 30.0 铁 69.0 乙 (1.0-X) C X  碳比X在0〜0.75的范围内变化。 在这种情况下,将磁性材料在873 K下热处理300秒。 在图 在图6中,横坐标表示外部磁场H ex  单位为MA / n,纵轴为特斯拉(T)的磁化强度J。 从图可以看出, 如图6所示,当X = 0.25时,获得了最佳的磁性,并且比根本没有添加碳的磁性材料更好。 \n\n [0084] 图。 图7是类似于图6的曲线图。 图6示出了由式Nd表示的R-T-B-C系稀土合金磁性材料的磁特性。 30.0 铁 59.0 有限公司 10.0 乙 (1.0-X) C X  碳比X在0〜0.75的范围内变化。 在这种情况下,磁性材料也在873 K热处理300秒。 从图可以看出, 如图7所示,在0.25至0.75的X范围内获得了足够好的磁性能。 \n\n [0085] 图。 图8示出了由式Nd表示的R-T-B-C基稀土合金磁性材料的磁性能。 30.0 铁 69.0 乙 0.75 C 0.25  热处理温度T在873K〜1,073K(即600℃〜800℃)的范围内变化。 从图可以看出, 如图8所示,当热处理温度为1,073K(或800℃)时,磁性能劣化。 \n\n [0086] 图。 图9表示以Nd为代表的R-T-B-C系稀土合金磁性材料的峰强度比。 30.0 铁 69.0 乙 0.75 C 0.25  或钕 30.0 铁 69.0 乙 0.50 C 0.50  热处理温度T在宽范围内变化。 从图可以看出,  9,比例(I 2.98 /一世 2.14 )的衍射峰强度I 2.98  第二化合物相(约2θ= 30.0度)对衍射峰强度I的影响 2.14  R的 2 铁 14 当热处理温度为约973K(或700℃)时,代表(410)面的B型结晶相最高。 \n\n 工业适用性 \n\n [0087] 根据本发明,提供了一种R-T-B-C系稀土合金磁性材料,其包含碳(C)但显示出优异的磁性。 因此,不管收集的稀土磁体是烧结磁体还是粘结磁体,都可以将收集的磁体再循环为磁性材料(细条或粉末形式)。 结果,可以更有效地利用宝贵的自然资源,并且可以显着降低磁体的制造成本。 \n\n [0088] 另外,添加剂碳降低稀土磁体的氧化反应性。 因此,磁体性能不会由于在制造过程中的发热或点火而劣化,或者不会危害制造过程的安全性。 此外,即使不在磁体表面上设置任何特殊的保护涂层以改善其耐候性,也可以使磁体随时间的劣化最小化。 ","18","2004-09-02","NEOMAX CO., LTD.","住友特殊金属株式会社","住友特殊金属株式会社","NEOMAX CO., LTD.","NEOMAX CO., LTD.","1","4-7-19, KITAHAMA, CHUO-KU, 541-0041, OSAKA-SHI, OSAKA, JAPAN"]
["当前申请(专利权)人地址","当前申请(专利权)人国家","原始申请(专利权)人地址","原始申请(专利权)人国家","发明人","第一发明人","发明人数量","第一发明人地址","发明人地址","权利要求","独立权利要求","权利要求(译)","权利要求数量","IPC分类号","IPC主分类号","UPC分类号","UPC主分类号","LOC分类号","CPC分类号"]
["4-7-19, KITAHAMA, CHUO-KU, 541-0041, OSAKA-SHI, OSAKA, JAPAN","JP","Osaka, JP","JP","TOMIZAWA, HIROYUKI | KANEKO, YUJI","TOMIZAWA, HIROYUKI","2","Hirakata, JP","Hirakata, JP | Uji, JP","1. An R-T-B-C based rare-earth alloy magnetic material (where R is at least one of the rare-earth elements including Y, T is a transition metal including iron as its main ingredient, B is boron, and C is carbon, an amount of R being 25 wt % to 35 wt % of the overall magnetic material, a total amount of B and C being 0.9 wt % to 1.1 wt % of the magnetic material, the balance of the magnetic material being T) comprising: a first compound phase with an R2Fe14B type crystal structure, and a second compound phase having a diffraction peak at a site with an interplanar spacing d of 0.295 nm to 0.300 nm, wherein the first compound phase is a main phase and an intensity ratio of the diffraction peak of the second compound phase to that of the first compound phase representing a (410) plane (and having an interplanar spacing of 0.214 nm) is at least 10%.\n\n2. The R-T-B-C based rare-earth alloy magnetic material of claim 1, wherein the ratio of the content of C (carbon) to the total content of B (boron) and C is 0.05 to 0.75.\n\n3. The R-T-B-C based rare-earth alloy magnetic material of claim 1, wherein the first compound phase has an average grain size of 10 nm to 500 nm.\n\n4. The R-T-B-C based rare-earth alloy magnetic material of claim 1, wherein the magnetic material is obtained by a method including the steps of: making a rapidly solidified alloy by rapidly quenching a melt of an R-T-B-C based rare-earth alloy; and thermally treating and crystallizing the rapidly solidified alloy.\n\n5. The R-T-B-C based rare-earth alloy magnetic material of claim 1, wherein a portion of Fe included in T is replaced with at least one element selected from the group consisting of Co, Ni, Mn, Cr and Al.\n\n6. The R-T-B-C based rare-earth alloy magnetic material of claim 1, further comprising, as an additive, at least one element selected from the group consisting of Si, P, Cu, Sn, Ti, Zr, V, Nb, Mo and Ga.\n\n7. A rare-earth alloy magnetic powder obtained by pulverizing the R-T-B-C based rare-earth alloy magnetic material of claim 1.\n\n8. A bonded magnet produced by processing the rare-earth alloy magnetic powder of claim 4.\n\n9. A permanent magnet produced by processing the rare-earth alloy magnetic powder of claim 7.\n\n10. A method of making an R-T-B-C based rare-earth alloy magnetic material, the method comprising the steps of: preparing a rapidly solidified alloy by rapidly quenching a melt of an R-T-B-C based rare-earth alloy (where R is at least one of the rare-earth elements including Y, T is a transition metal including iron as its main ingredient, B is boron, and C is carbon, an amount of R being 25 wt % to 35 wt % of the overall magnetic material, a total amount of B and C being 0.9 wt % to 1.1 wt % of the magnetic material, the balance of the magnetic material being T); and thermally treating and crystallizing the rapidly solidified alloy, wherein the step of thermally treating results in producing a first compound phase with an R2Fe14B type crystal structure and a second compound phase having a diffraction peak at a site with an interplanar spacing d of 0.295 nm to 0.300 nm, and wherein the first compound phase is a main phase and an intensity ratio of the diffraction peak of the second compound phase to that of the first compound phase representing a (410) plane is at least 10%.\n\n11. A method of making an R-T-B-C based rare-earth alloy magnetic material, the method comprising the step of obtaining the R-T-B-C based rare-earth alloy magnetic material, including a first compound phase with an R2Fe14B type crystal structure and a second compound phase having a diffraction peak at a site with an interplanar spacing d of 0.295 nm to 0.300 nm, by rapidly quenching a melt of an R-T-B-C based rare-earth alloy (where R is at least one of the rare-earth elements including Y, T is a transition metal including iron as its main ingredient, B is boron, and C is carbon, an amount of R being 25 wt % to 35 wt % of the overall magnetic material, a total amount of B and C being 0.9 wt % to 1.1 wt % of the magnetic material, the balance of the magnetic material being T), wherein the first compound phase is a main phase and an intensity ratio of the diffraction peak of the second compound phase to that of the first compound phase representing a (410) plane is at least 10%.\n\n12. The method of claim 10, further comprising a pulverizing process step before and/or after the step of thermally treating.\n\n13. A method for producing a bonded magnet, the method comprising the steps of: preparing a powder of the R-T-B-C based rare-earth alloy magnetic material that has been obtained by the method of one of claims 10 to 12; and compounding the powder and a binder material together and molding the compound.\n\n14. A method of making an R-T-B-C based rare-earth alloy magnetic material, the method comprising the steps of: preparing an R-T-B-C based rare-earth rapidly solidified alloy (where R is at least one of the rare-earth elements including Y, T is a transition metal including iron as its main ingredient, B is boron, and C is carbon, an amount of R being 25 wt % to 35 wt % of the overall magnetic material, a total amount of B and C being 0.9 wt % to 1.1 wt % of the magnetic material, the balance of the magnetic material being T) by melting and rapidly quenching and solidifying a collected and used R-T-B based rare-earth magnet; and thermally treating and crystallizing the R-T-B-C based rare-earth rapidly solidified alloy.\n\n15. The method of claim 14, wherein the step of thermally treating results in producing a first compound phase with an R2Fe14B type crystal structure and a second compound phase having a diffraction peak at a site with an interplanar spacing d of 0.295 nm to 0.300 nm, and wherein an intensity ratio of the diffraction peak of the second compound phase to that of the first compound phase representing a (410) plane is at least 10%.\n\n16. A method for producing a bonded magnet, the method comprising the steps of: preparing a powder of the R-T-B-C based rare-earth alloy magnetic material that has been obtained by the method of claim 14 or 15; and compounding the powder and a binder material together and molding the compound.","1. An R-T-B-C based rare-earth alloy magnetic material (where R is at least one of the rare-earth elements including Y, T is a transition metal including iron as its main ingredient, B is boron, and C is carbon, an amount of R being 25 wt % to 35 wt % of the overall magnetic material, a total amount of B and C being 0.9 wt % to 1.1 wt % of the magnetic material, the balance of the magnetic material being T) comprising: a first compound phase with an R2Fe14B type crystal structure, and a second compound phase having a diffraction peak at a site with an interplanar spacing d of 0.295 nm to 0.300 nm, wherein the first compound phase is a main phase and an intensity ratio of the diffraction peak of the second compound phase to that of the first compound phase representing a (410) plane (and having an interplanar spacing of 0.214 nm) is at least 10%.\n\n10. A method of making an R-T-B-C based rare-earth alloy magnetic material, the method comprising the steps of: preparing a rapidly solidified alloy by rapidly quenching a melt of an R-T-B-C based rare-earth alloy (where R is at least one of the rare-earth elements including Y, T is a transition metal including iron as its main ingredient, B is boron, and C is carbon, an amount of R being 25 wt % to 35 wt % of the overall magnetic material, a total amount of B and C being 0.9 wt % to 1.1 wt % of the magnetic material, the balance of the magnetic material being T); and thermally treating and crystallizing the rapidly solidified alloy, wherein the step of thermally treating results in producing a first compound phase with an R2Fe14B type crystal structure and a second compound phase having a diffraction peak at a site with an interplanar spacing d of 0.295 nm to 0.300 nm, and wherein the first compound phase is a main phase and an intensity ratio of the diffraction peak of the second compound phase to that of the first compound phase representing a (410) plane is at least 10%.\n\n11. A method of making an R-T-B-C based rare-earth alloy magnetic material, the method comprising the step of obtaining the R-T-B-C based rare-earth alloy magnetic material, including a first compound phase with an R2Fe14B type crystal structure and a second compound phase having a diffraction peak at a site with an interplanar spacing d of 0.295 nm to 0.300 nm, by rapidly quenching a melt of an R-T-B-C based rare-earth alloy (where R is at least one of the rare-earth elements including Y, T is a transition metal including iron as its main ingredient, B is boron, and C is carbon, an amount of R being 25 wt % to 35 wt % of the overall magnetic material, a total amount of B and C being 0.9 wt % to 1.1 wt % of the magnetic material, the balance of the magnetic material being T), wherein the first compound phase is a main phase and an intensity ratio of the diffraction peak of the second compound phase to that of the first compound phase representing a (410) plane is at least 10%.\n\n14. A method of making an R-T-B-C based rare-earth alloy magnetic material, the method comprising the steps of: preparing an R-T-B-C based rare-earth rapidly solidified alloy (where R is at least one of the rare-earth elements including Y, T is a transition metal including iron as its main ingredient, B is boron, and C is carbon, an amount of R being 25 wt % to 35 wt % of the overall magnetic material, a total amount of B and C being 0.9 wt % to 1.1 wt % of the magnetic material, the balance of the magnetic material being T) by melting and rapidly quenching and solidifying a collected and used R-T-B based rare-earth magnet; and thermally treating and crystallizing the R-T-B-C based rare-earth rapidly solidified alloy."," 1.基于R-T-B-C基稀土合金磁性材料(其中R是稀土元素中的至少一种包含Y,T是一种过渡金属,包括铁作为其主要成分,B是硼,C是碳,碳的量为整体磁性材料的25wt%至35wt%,B和C的总量为0.9Wt%至1.1wt%的磁性材料,磁性材料的平衡是t),包括:第一化合物相位,r2Fe.14B型晶体结构和第二化合物相,在具有0.295nm至0.300nm的平面间距D的位点上具有衍射峰的第二化合物相,其中第一化合物相是第二化合物的衍射峰的主相和强度比代表(410)平面(具有0.214nm的平面间隔)的第一化合物相的相位为至少10%。\n\n 2.根据权利要求1所述的基于R-T-B-C稀土合金磁性材料,那么C(碳)含量与B(硼)和C总含量的比例为0.05至0.75。\n\n 3.如权利要求1所述的基于R-T-B-C的稀土合金磁性材料,那么第一化合物相的平均晶粒尺寸为10nm至500nm。\n\n 4.如权利要求1所述的基于R-T-B-C稀土合金磁性材料,那么磁性材料通过包括以下步骤的方法获得:通过快速淬火基于R-T-B-C稀土合金的熔体制备快速凝固的合金;并热处理和结晶快速凝固的合金。\n\n 5.如权利要求1所述的基于R-T-B-C稀土合金磁性材料,那么将T中包含的Fe部分替换为选自Co,Ni,Mn,Cr和Al中的至少一种元素。\n\n 6.如权利要求1所述的基于R-T-B-C稀土合金磁性材料,进一步包括作为添加剂,至少一种选自Si,P,Cu,Sn,Ti,Zr,V,Nb,Mo和Ga的元素。\n\n7.一种稀土合金磁粉通过粉碎权利要求1的R-T-B-C基稀土合金磁性材磁性材料而获得的稀土合金磁粉。\n\n8.通过处理权利要求4的稀土合金磁粉制备的粘合磁铁。\n\n9.一种通过加工权利要求7的稀土合金磁粉生产的永磁体。\n\n 10.一种制备基于R-T-B-C稀土合金磁性材料的方法,该方法包括步骤:通过快速淬火基于RTBC基稀土合金的熔体制备快速凝固的合金(其中R是包括Y,T的稀土元素中的至少一个是包括铁作为其主要成分的过渡金属, B是硼,C是碳,r的量为25wt%至35wt%的整个磁性材料,B和C的总量为0.9wt%至1.1wt%的磁性材料,平衡磁性材料是t);热处理和结晶快速凝固的合金,其中热处理的步骤导致用R的产生第一化合物相2Fe.14B型晶体结构和具有衍射峰的衍射峰在位点上,平面间隔为0.295nm至0.300nm,并且其中第一化合物相是第二化合物的衍射峰的主相和强度比代表(410)平面的第一化合物相的相位为至少10%。\n\n 11.一种制备基于R-T-B-C稀土合金磁性材料的方法,该方法包括获得基于R-T-B-C稀土合金磁性材料的步骤,包括具有R的第一化合物相2Fe.14B型晶体结构和第二化合物相,通过快速猝灭基于RTBC基稀土合金的熔体(其中R是至少一个)的熔体(其中r至少一个),具有0.295nm至0.300nm的衍射峰。包括Y,T的稀土元素是作为其主要成分的铁的过渡金属,B是硼,C是碳,碳的量为整体磁性材料的25wt%至35wt%,总量为B和C为磁性材料的0.9wt%至1.1wt%,磁性材料的平衡为t),其中第一化合物相是主相和第二化合物衍射峰与该主相和强度比代表(410)平面的第一化合物阶段至少为10%。\n\n 12.如权利要求10所述的方法,还包括在热处理步骤之前和/或之后的粉碎过程步骤。\n\n 13.一种制造粘合磁体的方法,方法包括以下步骤:制备通过权利要求10至12中任一项的方法获得的R-T-B-C基稀土合金磁性材料的粉末;并将粉末和粘合剂材料混合在一起并模塑化合物。\n\n 14.一种制备基于R-T-B-C基稀土合金磁性材料的方法,该方法包括以下步骤:制备基于RTBC基于稀土的纯固化合金(其中R是包括Y,T的稀土元素中的至少一个是包括铁作为其主要成分的过渡金属,B是硼,C是碳,R为总磁性材料的25wt%至35wt%的量,B和C的总量为磁性材料的0.9wt%至1.1wt%,磁性材料的平衡是通过熔化的并迅速淬火并凝固收集的基于RTB的稀土磁铁;并热处理和结晶基于R-T-B-C稀土的稀有凝固合金。\n\n 15.如权利要求14所述的方法,那么热处理的步骤导致生产第一化合物相和R.2Fe.14B型晶体结构和第二化合物相,在位点处具有衍射峰,平面间隔为0.295nm至0.300nm,并且其中第二化合物相的衍射峰与代表第一化合物相的衍射峰的强度比A(410)平面至少为10%。\n\n 16.一种制造粘合磁体的方法,方法包括步骤:制备通过权利要求14或15的方法获得的R-T-B-C基稀土合金磁性材料的粉末;并将粉末和粘合剂材料混合在一起并模塑化合物。","16","H01F1/053 | H01F1/057 | B22F1/00 | B22F9/10 | B22F8/00 | C22C33/02 | C22C38/00 | H01F1/04 | H01F1/058 | H01F1/06 | H01F1/08","H01F1/053","148/301 | 148/101 | 148/121 | 148/302 | 420/121 | 420/83 | 148/104","148/301","-","H01F41/0266 | H01F1/058 | H01F1/0578"]
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