WO2021135143A1 - R-t-b系烧结磁体及其制备方法 - Google Patents

R-t-b系烧结磁体及其制备方法 Download PDF

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WO2021135143A1
WO2021135143A1 PCT/CN2020/100575 CN2020100575W WO2021135143A1 WO 2021135143 A1 WO2021135143 A1 WO 2021135143A1 CN 2020100575 W CN2020100575 W CN 2020100575W WO 2021135143 A1 WO2021135143 A1 WO 2021135143A1
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content
sintered magnet
rtb
based sintered
percentage
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PCT/CN2020/100575
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French (fr)
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施尧
蓝琴
黄佳莹
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厦门钨业股份有限公司
福建省长汀金龙稀土有限公司
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Priority to EP20909158.6A priority Critical patent/EP4086924A4/en
Priority to US17/784,996 priority patent/US20230021772A1/en
Priority to JP2022539202A priority patent/JP7312916B2/ja
Publication of WO2021135143A1 publication Critical patent/WO2021135143A1/zh

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    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/032—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials
    • H01F1/04—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of hard-magnetic materials metals or alloys
    • H01F1/047—Alloys characterised by their composition
    • H01F1/053—Alloys characterised by their composition containing rare earth metals
    • H01F1/055—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5
    • H01F1/057—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B
    • H01F1/0571—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes
    • H01F1/0575—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together
    • H01F1/0577—Alloys characterised by their composition containing rare earth metals and magnetic transition metals, e.g. SmCo5 and IIIa elements, e.g. Nd2Fe14B in the form of particles, e.g. rapid quenched powders or ribbon flakes pressed, sintered or bonded together sintered
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    • H01F41/0293—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets for manufacturing permanent magnets diffusion of rare earth elements, e.g. Tb, Dy or Ho, into permanent magnets
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Definitions

  • the invention relates to an R-T-B series sintered magnet and a preparation method thereof.
  • RTB series sintered magnets (R refers to rare earth elements, T refers to transition metal elements and metal elements of the third main group, B refers to boron element) are widely used in electronic products, automobiles, wind power, home appliances, elevators and Industrial robots and other fields, such as hard disks, mobile phones, earphones, and permanent magnet motors such as elevator traction machines, generators, etc., are used as energy sources, and their demand is increasing. ), the requirements for coercivity performance are gradually increasing.
  • R-T-B based sintered magnets with high coercivity without adding or adding a small amount of heavy rare earths.
  • the patent CN106128673A prepared a sintered neodymium iron boron magnet (remanence 12.77kGs, coercivity 22.42kOe). But its B content is higher, it will generate more B-rich phase, and then affect the product's remanence performance. This status quo needs to be resolved urgently.
  • the technical problem to be solved by the present invention is to solve the problem that it is difficult to prepare high coercivity and high remanence RTB based sintered magnets in the prior art without adding or adding a small amount of heavy rare earth (addition of heavy rare earth RH ⁇ 1)
  • the problem of RTB series sintered magnet and its preparation method are provided.
  • the present invention suppresses the precipitation of R 2 Fe 17 phase by adding a small amount of Ti, and the joint addition of Ga, Al, Cu, and Co without adding or adding a small amount of heavy rare earths, and generates high levels in the grain boundaries during the aging process.
  • the Cu low Al phase R x -(Cu a -Ga b -Al c ) y greatly increases the coercivity of the magnet.
  • the present invention solves the above technical problems through the following technical solutions.
  • the present invention discloses an R-T-B series sintered magnet, which contains: R, B, Ti, Ga, Al, Cu, and T, the content of which is as follows:
  • the content of R is 29.0 ⁇ 33%
  • the content of B is 0.86 ⁇ 0.93%
  • the content of Ti is 0.05 to 0.25%
  • the content of Ga is 0.3-0.5%, but not 0.5%;
  • the content of Al is 0.6-1%, but not 0.6%;
  • the content of Cu is 0.36 ⁇ 0.55%
  • R is a rare earth element containing at least Nd
  • B is boron
  • Ti is titanium
  • Ga gallium
  • Al is aluminum
  • Cu is copper
  • T contains Fe and Co; the percentages are mass percentages.
  • the content of R can be conventional in the art.
  • the content of R is 30.2-33%, for example, 30.2%, 31.5%, 33%; the percentage is a mass percentage.
  • the R is a rare earth element including a heavy rare earth element RH.
  • the content of RH in the R is 0 or not more than 1%, for example, 0% or 0.5%; the percentage is a mass percentage.
  • the content of B is between 0.86% and 0.93%. If the content of B is less than 0.86%, the squareness of the magnet will become worse; if the content of B is greater than 0.93%, high performance cannot be achieved.
  • the content of B is 0.915% to 0.93%, such as 0.915%, 0.92%, or 0.93%; the percentage is a mass percentage.
  • the RTB-based sintered magnet includes a main phase and a grain boundary phase; wherein, the main phase includes R 2 T 14 B, and the grain boundary phase includes R x -(Cu a -Ga b -Al c ) y and rare earth oxidation phase;
  • the content of the main phase is 94-98%; the content of the R x -(Cu a -Ga b -Al c ) y is 1 to 3.5%; the content of the rare earth oxidation phase is 1 to 2.5%, so The stated percentages are volume percentages.
  • the precipitation of R 2 T 17 is effectively suppressed.
  • the grain boundary phase R x -(Cu a -Ga b -Al c ) y the formation of this phase can modify the grain boundary, improve the infiltration angle and fluidity of the grain boundary phase, and make the grain boundary phase in the main phase
  • the flow between the particles is easier, and the grain boundary phase becomes thinner and continuous, which not only plays the role of demagnetization coupling but also increases the volume fraction of the main phase, resulting in a magnet with excellent Br and Hcj.
  • the rare earth oxide phase as known to those skilled in the art, is obtained due to an inevitable oxidation reaction.
  • the content of Ti is 0.15 to 0.25%, for example, 0.15%, 0.2%, 0.25%; the percentage is a mass percentage.
  • the content of Ga is 0.3-0.455%, for example, 0.3%, 0.4%, 0.455%; the percentage is a mass percentage.
  • the content of Al is 0.65-1%, but not 1%, such as 0.65%, 0.7%, 0.8%, 0.9%; the percentage is a mass percentage.
  • the content of Cu is 0.45-0.55%, for example, 0.45%, 0.5%, 0.55%; the percentage is a mass percentage.
  • the content of Fe and Co is conventional in the art.
  • the content of Fe and Co is the balance of 100% by mass; the percentage is by mass.
  • the content of Co is 0.5-3%, such as 0.5%, 1.5%, or 3.0%; the percentage is a mass percentage.
  • the content of Fe is 60-68%; the percentage is mass percentage.
  • the R-T-B series sintered magnet contains unavoidable impurities and O, N or C introduced during the preparation process.
  • the total content of C, N and O in the R-T-B sintered magnet is 1000 ppm to 3500 ppm.
  • the RTB-based sintered magnet includes: Nd content is 31.5%, B content is 0.92%, Co content is 0.5%; Al content is 0.9%, Cu content is The content of Ga is 0.45%, the content of Ga is 0.455%, the content of Ti is 0.2%, and Fe is the balance; the percentage is the mass percentage.
  • the RTB-based sintered magnet includes: Nd content of 31.5%, B content of 0.92%, Co content of 0.5%; Al content of 1.0%, Cu content
  • the content of Ga is 0.5%
  • the content of Ga is 0.455%
  • the content of Ti is 0.2%
  • Fe is the balance; the percentage is the mass percentage.
  • the RTB-based sintered magnet includes: Nd content of 31.5%, Dy content of 0.5%; B content of 0.915%, Co content of 0.5%; Al content
  • the content of Cu is 0.7%, the content of Cu is 0.55%, the content of Ga is 0.455%, the content of Ti is 0.25%, and Fe is the balance; the percentages are mass percentages.
  • the RTB-based sintered magnet includes: Nd content of 30.2%, B content of 0.93%, Co content of 1.5%; Al content of 0.65%, Cu content The percentage is 0.4%, the content of Ga is 0.3%, the content of Ti is 0.15%, and Fe is the balance; the percentage is the mass percentage.
  • the RTB-based sintered magnet includes: the content of Nd is 33%, the content of B is 0.86%, the content of Co is 3.0%, the content of Al is 0.8%, and the content of Cu It is 0.36%, the content of Ga is 0.4%, the content of Ti is 0.05%, and Fe is the balance; the percentage is the mass percentage.
  • the present invention also provides an RTB-based sintered magnet, which is characterized in that it comprises a main phase and a grain boundary phase; wherein the main phase comprises R 2 T 14 B, and the grain boundary phase comprises R x -(Cu a -Ga b -Al c ) y and rare earth oxidation phase;
  • the content of the main phase is 94-98%; the content of the R x -(Cu a -Ga b -Al c ) y is 1 to 3.5%; the content of the rare earth oxidation phase is 1 to 2.5%, so The stated percentages are volume percentages.
  • x/y 1.5 ⁇ 3
  • a:b:c (10 ⁇ 40):(6 ⁇ 19) :1.
  • the invention also discloses a method for preparing the RTB-based sintered magnet as described above, and the steps include: sequentially smelting, casting, hydrogen breaking, jet milling, molding, sintering and aging of the raw materials of the RTB-based sintered magnet, namely can.
  • the raw material of the R-T-B sintered magnet is known to those skilled in the art as a raw material that satisfies the element content of the R-T-B sintered magnet as described above.
  • the operation and conditions of the smelting can be conventional in the art.
  • the raw materials are smelted in a high-frequency vacuum melting furnace.
  • the vacuum degree of the smelting furnace is less than 0.1Pa.
  • the vacuum degree of the melting furnace is less than 0.02 Pa.
  • the melting temperature is 1450-1550°C.
  • the melting temperature is 1500-1550°C.
  • the operation and conditions of the casting can be conventional in the art, and are generally carried out in an inert atmosphere to obtain R-T-B alloy cast pieces.
  • the casting is performed under Ar atmosphere conditions.
  • the atmospheric pressure of the casting is 20-70 kPa.
  • the atmospheric pressure of the casting is 30-50 kPa.
  • the rotational speed of the cast copper roll is 0.4-2m/s, for example, 1m/s.
  • the thickness of the R-T-B alloy cast piece obtained by casting is 0.15-0.5 mm.
  • the thickness of the R-T-B alloy slab obtained by casting is 0.2 to 0.35 mm, for example, 0.25 mm.
  • the operation and conditions of the hydrogen breaker can be conventional in the art.
  • the hydrogen breakage includes a hydrogen adsorption process and a dehydrogenation process, and the R-T-B alloy cast piece can be subjected to hydrogen breakage treatment to obtain R-T-B alloy powder.
  • the hydrogen absorption temperature of the hydrogen breaker is 20 to 300°C, for example, 25°C.
  • the hydrogen absorption pressure of the hydrogen breaker is 0.12 to 0.19 MPa, for example, 0.19 MPa.
  • the dehydrogenation time of the hydrogen breaking is 0.5-5h, for example 2h.
  • the dehydrogenation temperature of the hydrogen breakdown is 450-600°C, for example, 550°C.
  • the operation and conditions of the jet mill can be conventional in the art.
  • the jet mill is to send the R-T-B alloy powder into a jet mill for jet milling to continue to be crushed to obtain fine powder.
  • the grinding pressure of the jet mill is 0.3-0.5 MPa, for example 0.4 MPa.
  • the median particle size D50 of the fine powder is 3 to 5.5 ⁇ m, for example, 4 ⁇ m.
  • the molding operation and conditions can be conventional in the art.
  • the molding is performed at a magnetic field strength above 1.8T, such as 1.8T, and under the protection of a nitrogen atmosphere.
  • the sintering operation and conditions can be conventional in the art.
  • the sintering is divided into four steps:
  • the growth of crystal grains can be suppressed, and the sintering temperature range can be expanded to a certain extent.
  • the aging operation and conditions can be conventional in the art.
  • the aging includes primary aging and secondary aging.
  • the temperature of the primary aging is 850°C to 950°C, for example, 900°C.
  • the secondary aging temperature is 440°C to 540°C, for example, 480°C.
  • the secondary aging temperature range of the magnet under this composition can be 440°C to 540°C, and the fluctuation space of 100°C can be obtained, which is beneficial to mass production.
  • the invention also provides an R-T-B series sintered magnet, which is prepared by the aforementioned preparation method.
  • the present invention also provides an application of the aforementioned R-T-B series sintered magnet in a motor as a motor rotor magnet.
  • the reagents and raw materials used in the present invention are all commercially available.
  • the present invention uses low B technology to adjust the ratio of Ti, Ga, Al, Cu and Co in the composition without adding or adding a small amount of heavy rare earth (heavy rare earth RH addition ⁇ 1), and its synergistic effect And the grain boundary phase R x -(Cu a -Ga b -Al c ) y with high Cu and low Al is formed during the aging process, which adjusts the structure of the grain boundary phase and greatly improves the coercivity and remanence.
  • FIG. 1 is an EPMA chart of the R-T-B sintered magnet of Example 1.
  • R-T-B series sintered magnet The preparation method of R-T-B series sintered magnet is as follows:
  • the raw materials are smelted in a high-frequency vacuum smelting furnace, the vacuum of the smelting furnace is less than 0.02 Pa, and the melting temperature is 1500-1550°C.
  • the casting atmosphere pressure is 30-50kPa, and the casting copper roll speed is 1m/s.
  • the thickness of the cast R-T-B alloy slab is 0.25 mm.
  • the dehydrogenation time of hydrogen breakdown is 2h.
  • the dehydrogenation temperature is 550°C to obtain R-T-B alloy powder.
  • Jet mill Send the R-T-B alloy powder to the jet mill for jet mill to continue to be crushed to obtain fine powder.
  • the grinding pressure of the jet mill is 0.4MPa.
  • the median particle diameter D50 of the obtained fine powder was 4 ⁇ m.
  • Forming The fine powder is oriented and formed under a certain magnetic field strength to obtain a compact.
  • the molding is carried out under the protection of 1.8T magnetic field strength and nitrogen atmosphere.
  • the temperature of primary aging is 900°C; the temperature of secondary aging is 480°C.
  • Figure 1 shows the microscopic analysis results of the field emission electron probe microanalyzer (EPMA) of Example 1.
  • Table 2 shows the microscopic analysis results of the R-T-B based sintered magnets in Examples 1 to 5 and Comparative Example 8.

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Abstract

R-T-B系烧结磁体及其制备方法。该R-T-B系烧结磁体包含：R、B、Ti、Ga、Al、Cu和T，其含量如下：R的含量为29.0～33％；B的含量为0.86～0.93％；Ti的含量为0.05～0.25％；Ga的含量为0.3～0.5％，但不为0.5％；Al的含量为0.6～1％，但不为0.6％；Cu的含量为0.36～0.55％；所述百分比为质量百分比。通过采用低B技术，在不添加或少量添加重稀土的情况下，既提高了R-T-B系烧结磁体的剩磁性能，也保证了磁体的矫顽力和方形度。

Description

R-T-B系烧结磁体及其制备方法
本申请要求申请日为2019年12月31日的中国专利申请CN201911423952.3的优先权。本申请引用上述中国专利申请的全文。
技术领域
本发明涉及R-T-B系烧结磁体及其制备方法。
背景技术
R-T-B系烧结磁铁(R指稀土元素，T指过渡金属元素及第三主族金属元素，B指硼元素)由于其优异的磁特性而被广泛应用于电子产品、汽车、风电、家电、电梯及工业机器人等领域，例如硬盘、手机、耳机、和电梯曳引机、发电机等永磁电机中作为能量源等，其需求日益扩大，且各产商对于磁铁性能例如剩磁(remanence，简称Br)、矫顽力性能的要求也逐步提升。
实验中发现，在R-T-B系烧结磁体制备的过程中容易析出R 2Fe 17相，进而使得磁体的矫顽力性能劣化。现有技术中，有通过添加重稀土元素例如Dy、Tb、Gd等，以提高材料的矫顽力以及改善温度系数，但重稀土价格高昂，采用这种方法提高R-T-B系烧结磁体产品的矫顽力，会增加原材料成本，不利于R-T-B系烧结磁体的应用。
因此，需要在不添加或少量添加重稀土的情况下，制备得到高矫顽力的R-T-B系烧结磁铁。例如专利CN106128673A，制备了烧结钕铁硼磁体(剩磁12.77kGs、矫顽力22.42kOe)。但是其B含量较高，会生成较多的富B相，进而影响到产品的剩磁性能。该现状亟待解决。
发明内容
本发明所要解决的技术问题在于解决现有技术中在不添加或少量添加重稀土(重稀 土RH添加量≤1)的情况下，难以制备得到高矫顽力且高剩磁的R-T-B系烧结磁铁的问题，而提供了R-T-B系烧结磁体及其制备方法。本发明在不添加或少量添加重稀土的情况下，通过微量的Ti、以及Ga、Al、Cu和Co的联合添加，抑制R 2Fe 17相的析出，并在时效过程中在晶界生成高Cu低Al相R x-(Cu a-Ga b-Al c) y，大幅提升了磁体的矫顽力。
本发明通过以下技术方案解决上述技术问题。
本发明公开了R-T-B系烧结磁体，其包含：R、B、Ti、Ga、Al、Cu和T，其含量如下：
R的含量为29.0～33％；
B的含量为0.86～0.93％；
Ti的含量为0.05～0.25％；
Ga的含量为0.3～0.5％，但不为0.5％；
Al的含量为0.6～1％，但不为0.6％；
Cu的含量为0.36～0.55％；
其中，R为至少含有Nd的稀土元素，B为硼，Ti为钛，Ga为镓，Al为铝，Cu为铜，T包含Fe和Co；所述百分比为质量百分比。
本发明中，所述R的含量可为本领域常规。较佳地，所述R的含量为30.2～33％，例如为30.2％、31.5％、33％；所述百分比为质量百分比。
本发明中，所述R为包含重稀土元素RH的稀土元素。较佳地，所述R中，RH的含量为0或不大于1％，例如为0％、0.5％；所述百分比为质量百分比。
本发明中，采用低B技术，可有效地实现在无重稀土或重稀土添加量(RH＝0或RH≤1)较少的情况下，得到高性能R-T-B系烧结磁体。本发明中，B的含量在0.86～0.93％之间，若B含量小于0.86％的话，磁体的方形度会变的较差；B含量大于0.93％的话，达不到高性能。
较佳地，所述B的含量为0.915～0.93％，例如为0.915％、0.92％、0.93％；所述百分比为质量百分比。
本发明中，较佳地，所述R-T-B系烧结磁体包含主相和晶界相；其中，所述主相包含R 2T 14B，所述晶界相包含R x-(Cu a-Ga b-Al c) y和稀土氧化相；
其中，x/y＝1.5～3；a/b＝2～5；(a+b)/c＝30～70；
所述主相的含量为94～98％；所述R x-(Cu a-Ga b-Al c) y的含量为1～3.5％；所述稀土氧化相的含量为1～2.5％，所述百分比为体积百分比。
更佳地，所述晶界相R x-(Cu a-Ga b-Al c) y中，x/y＝1.5～3，a:b:c＝(10～40):(6～19):1。
本发明中，通过Ti、Ga、Al、Cu的适量添加，有效地抑制了R 2T 17的析出。发明人发现，虽然加入了较多的Al，但由于微量的Ti的一同添加，制得的R-T-B系烧结磁体在晶界并没有形成高Al的晶界相，而是形成了高Cu低Al的晶界相R x-(Cu a-Ga b-Al c) y，该相的生成可起到修饰晶界的作用，改善晶界相的浸润角以及流动性，使得晶界相在主相之间流动更为容易，进而晶界相变得轻薄连续，既起到去磁耦合的作用又增加了主相的体积分数，得到了Br与Hcj均优异的磁体。其中，所述氧化稀土相，本领域技术人员知晓，是由于不可避免的氧化反应而得。
较佳地，所述Ti的含量为0.15～0.25％，例如为0.15％、0.2％、0.25％；所述百分比为质量百分比。
较佳地，所述Ga的含量为0.3～0.455％，例如为0.3％、0.4％、0.455％；所述百分比为质量百分比。
较佳地，所述Al的含量为0.65～1％，但不为1％，例如为0.65％、0.7％、0.8％、0.9％；所述百分比为质量百分比。
较佳地，所述Cu的含量为0.45～0.55％，例如为0.45％、0.5％、0.55％；所述百分比为质量百分比。
本发明中，所述Fe和Co的含量为本领域常规。
较佳地，所述Fe和Co的含量为占100％质量百分比的余量；所述百分比为质量百分比。
更佳地，所述Co的含量为0.5～3％，例如为0.5％、1.5％、3.0％；所述百分比为质量百分比。
更佳地，所述Fe的含量为60～68％；所述百分比为质量百分比。
本发明中，所述R-T-B系烧结磁体包含不可避免的杂质以及制备过程中引入的O、N或C。
较佳地，所述R-T-B系烧结磁体中C、N和O的含量总和为1000ppm～3500ppm。
在本发明一优选实施方式中，所述R-T-B系烧结磁体，其包含：Nd的含量为31.5％，B的含量为0.92％，Co的含量为0.5％；Al的含量为0.9％，Cu的含量为0.45％，Ga的含量为0.455％，Ti的含量为0.2％，Fe为余量；所述百分比为质量百分比。
在本发明一优选实施方式中，所述R-T-B系烧结磁体，其包含：Nd的含量为31.5％，B的含量为0.92％，Co的含量为0.5％；Al的含量为1.0％，Cu的含量为0.5％，Ga的含量为0.455％，Ti的含量为0.2％，Fe为余量；所述百分比为质量百分比。
在本发明一优选实施方式中，所述R-T-B系烧结磁体，其包含：Nd的含量为31.5％，Dy的含量为0.5％；B的含量为0.915％，Co的含量为0.5％；Al的含量为0.7％，Cu的含量为0.55％，Ga的含量为0.455％，Ti的含量为0.25％，Fe为余量；所述百分比为质量百分比。
在本发明一优选实施方式中，所述R-T-B系烧结磁体，其包含：Nd的含量为30.2％，B的含量为0.93％，Co的含量为1.5％；Al的含量为0.65％，Cu的含量为0.4％，Ga的含量为0.3％，Ti的含量为0.15％，Fe为余量；所述百分比为质量百分比。
在本发明一优选实施方式中，所述R-T-B系烧结磁体，其包含：Nd的含量为33％，B的含量为0.86％，Co的含量为3.0％；Al的含量为0.8％，Cu的含量为0.36％，Ga的含量为0.4％，Ti的含量为0.05％，Fe为余量；所述百分比为质量百分比。
本发明还提供了R-T-B系烧结磁体，其特征在于，其包含主相和晶界相；其中，所述主相包含R 2T 14B，所述晶界相包含R x-(Cu a-Ga b-Al c) y和稀土氧化相；
其中，x/y＝1.5～3；a/b＝2～5；(a+b)/c＝30～70；
所述主相的含量为94～98％；所述R x-(Cu a-Ga b-Al c) y的含量为1～3.5％；所述稀土氧化相的含量为1～2.5％，所述百分比为体积百分比。
较佳地，所述晶界相R x-(Cu a-Ga b-Al c) y中，x/y＝1.5～3，a:b:c＝(10～40):(6～19):1。
本发明还公开了一种如前所述的R-T-B系烧结磁体的制备方法，其步骤包括：将R-T-B系烧结磁体的原料依次进行熔炼、铸造、氢破、气流磨、成型、烧结和时效，即可。
本发明中，所述R-T-B系烧结磁体的原料，本领域技术人员知晓为满足如前所述 R-T-B系烧结磁体的元素含量质量百分比的原料。
本发明中，所述熔炼的操作和条件可为本领域常规。
较佳地，在高频真空熔炼炉中，将所述原料熔炼。
较佳地，所述熔炼炉的真空度小于0.1Pa。
更佳地，所述熔炼炉的真空度小于0.02Pa。
较佳地，所述熔炼的温度为1450～1550℃。
更佳地，所述熔炼的温度为1500～1550℃。
本发明中，所述铸造的操作和条件可为本领域常规，一般在惰性气氛中进行，得到R-T-B合金铸片。
较佳地，所述铸造在Ar气氛条件下进行。
较佳地，所述铸造的气氛压力为20～70kPa。
更佳地，所述铸造的气氛压力为30～50kPa。
较佳地，所述铸造的铜辊转速为0.4～2m/s，例如为1m/s。
较佳地，所述铸造得到的R-T-B合金铸片的厚度为0.15～0.5mm。
更佳地，所述铸造得到的R-T-B合金铸片的厚度为0.2～0.35mm，例如为0.25mm。
本发明中，所述氢破的操作和条件可为本领域常规。一般情况下，所述氢破包括氢吸附过程和脱氢过程，可将所述R-T-B合金铸片进行氢破处理，获得R-T-B合金粉体。
较佳地，所述氢破的吸氢温度为20～300℃，例如为25℃。
较佳地，所述氢破的吸氢压力为0.12～0.19MPa，例如为0.19MPa。
较佳地，所述氢破的脱氢时间为0.5～5h，例如为2h。
较佳地，所述氢破的脱氢温度为450～600℃，例如为550℃。
本发明中，所述气流磨的操作和条件可为本领域常规。较佳地，所述气流磨为将所述R-T-B合金粉体送入气流磨机进行气流磨继续破碎，得到细粉。
更佳地，所述气流磨的研磨压力为0.3～0.5MPa，例如为0.4MPa。
更佳地，所述细粉的中值粒径D50为3～5.5μm，例如为4μm。
本发明中，所述成型的操作和条件可为本领域常规。
较佳地，所述成型在1.8T以上的，例如为1.8T的磁场强度和氮气气氛保护下进行。
本发明中，所述烧结的操作和条件可为本领域常规。
较佳地，所述烧结分为四步：
(1)升高温度至150～300℃，保温时间为1～4h；
(2)升高温度至400～600℃，保温时间为1～4h；
(3)升高温度至800～900℃，保温时间为1～4h；
(4)升高温度至1000～1090℃，保温时间大于3h。
本发明一优选实施例中，由于Ti的微量添加，可抑制晶粒长大，可一定程度上的扩大烧结的温度范围。
本发明中，所述时效的操作和条件可为本领域常规。
较佳地，所述时效包含一级时效和二级时效。
更佳地，所述一级时效的温度为850℃～950℃，例如为900℃。
更佳地，所述二级时效温度为440℃～540℃，例如为480℃。
本发明一优选实施例中，由于Al的添加量较高，使得该成分下的磁体二级时效温度范围可为440℃～540℃，可100℃的波动空间，利于量产。
本发明还提供了一种R-T-B系烧结磁体，其由如前所述的制备方法制备得到。
本发明还提供了一种如前所述的R-T-B系烧结磁体在电机中作为电机转子磁钢的应用。
在符合本领域常识的基础上，上述各优选条件，可任意组合，即得本发明各较佳实例。
本发明所用试剂和原料均市售可得。
本发明的积极进步效果在于：
本发明通过采用低B技术，在不添加或少量添加重稀土(重稀土RH添加量≤1)的情况下，对成分中的Ti、Ga、Al、Cu和Co的比列调整，其协同作用以及时效过程中形成高Cu低Al的晶界相R x-(Cu a-Ga b-Al c) y，调节了晶界相的结构，大幅提升了矫顽力和剩磁。
附图说明
图1为实施例1的R-T-B系烧结磁体的EPMA图谱。
具体实施方式
下面通过实施例的方式进一步说明本发明，但并不因此将本发明限制在所述的实施例范围之中。下列实施例中未注明具体条件的实验方法，按照常规方法和条件，或按照商品说明书选择。
各实施例1～5和对比例6～12中的R-T-B系烧结磁体中的元素质量百分比和磁性能如下表1所示。表2中，“Br”为剩余磁化强度，“Hcj”为内禀矫顽力(intrinsic coercivity)，Hk/Hcj为方形度(squareness ratio)，“/”表示未添加该元素。
表1 R-T-B系烧结磁体中的元素质量百分比和磁性能
Figure PCTCN2020100575-appb-000001
实施例1
R-T-B系烧结磁体制备方法如下：
(1)熔炼：按表1所示的各实施例和对比例的元素质量百分比，配置满足该元素质量百分比的原料配方。
将原料于高频真空熔炼炉中进行熔炼，熔炼炉的真空度小于0.02Pa，熔炼的温度为1500～1550℃。
(2)铸造：在Ar中进行，得到R-T-B合金铸片。
铸造的气氛压力为30～50kPa，铸造的铜辊转速为1m/s。
铸造得到的R-T-B合金铸片的厚度为0.25mm。
(3)氢破：R-T-B合金铸片的氢吸附过程的吸氢温度为25℃；吸氢压力为0.19MPa。
氢破的脱氢时间为2h。脱氢温度为550℃，获得R-T-B合金粉体。
(4)气流磨：将所述R-T-B合金粉体送入气流磨机进行气流磨继续破碎，得到细粉。
气流磨的研磨压力为0.4MPa。
得到的细粉的中值粒径D50为4μm。
(5)成型：细粉在一定磁场强度下经取向成型得到压坯。
成型在1.8T的磁场强度和氮气气氛保护下进行。
(6)烧结，分为四步(本批次样品量为10公斤)：
①升高温度至150～300℃，保温时间为2h；
②升高温度至400～600℃，保温时间为2h；
③升高温度至800～900℃，保温时间为4h；
④升高温度至1000～1090℃，保温时间为5h。
(7)时效
一级时效的温度为900℃；二级时效的温度为480℃。
实施例2～5和对比例6～12制备工艺除选用的原料配方不同以外，制备工艺中的参数与实施例1的制备工艺相同。
效果实施例
图1为实施例1的场发射电子探针显微分析仪(EPMA)微观分析结果。
实施例1～5和对比例8中的R-T-B系烧结磁体的微观分析结果如表2所示。
表2 R-T-B系烧结磁体的微观分析结果
Figure PCTCN2020100575-appb-000002

Claims (10)

  1. 一种R-T-B系烧结磁体，其特征在于，其包含：R、B、Ti、Ga、Al、Cu和T，其含量如下：
    R的含量为29.0～33％；
    B的含量为0.86～0.93％；
    Ti的含量为0.05～0.25％；
    Ga的含量为0.3～0.5％，但不为0.5％；
    Al的含量为0.6～1％，但不为0.6％；
    Cu的含量为0.36～0.55％；
    其中，R为至少含有Nd的稀土元素，B为硼，Ti为钛，Ga为镓，Al为铝，Cu为铜，T包含Fe和Co；所述百分比为质量百分比。
  2. 如权利要求1所述的R-T-B系烧结磁体，其特征在于，所述R的含量为30.2～33％，例如为30.2％、31.5％、33％；
    和/或，所述R中，RH的含量为0或不大于1％，例如为0％、0.5％；
    和/或，所述B的含量为0.915～0.93％，例如为0.915％、0.92％、0.93％；
    和/或，所述Ti的含量为0.15～0.25％，例如为0.15％、0.2％、0.25％；
    和/或，所述Ga的含量为0.3～0.455％，例如为0.3％、0.4％、0.455％；
    和/或，所述Al的含量为0.65～1％，但不为1％，例如为0.65％、0.7％、0.8％、0.9％；
    和/或，所述Cu的含量为0.45～0.55％，例如为0.45％、0.5％、0.55％；
    和/或，所述Fe和Co的含量为占100％质量百分比的余量；
    较佳地，所述Co的含量为0.5～3％，例如为0.5％、1.5％、3.0％；
    较佳地，所述Fe的含量为60～68％；
    和/或，所述R-T-B系烧结磁体中C、N和O的含量总和为1000ppm～3500ppm；
    所述百分比为质量百分比。
  3. 如权利要求1所述的R-T-B系烧结磁体，其特征在于，所述R-T-B系烧结磁体包含主相和晶界相；其中，所述主相包含R 2T 14B，所述晶界相包含R x-(Cu a-Ga b-Al c) y和稀土氧化相；
    其中，x/y＝1.5～3；a/b＝2～5；(a+b)/c＝30～70；
    所述主相的含量为94～98％；所述R x-(Cu a-Ga b-Al c) y的含量为1～3.5％；所述稀土氧化相的含量为1～2.5％，所述百分比为体积百分比；
    较佳地，所述晶界相R x-(Cu a-Ga b-Al c) y中，x/y＝1.5～3，a:b:c＝(10～40):(6～19):1。
  4. 如权利要求1所述的R-T-B系烧结磁体，其特征在于，所述R-T-B系烧结磁体，其包含：Nd的含量为31.5％，B的含量为0.92％，Co的含量为0.5％；Al的含量为0.9％，Cu的含量为0.45％，Ga的含量为0.455％，Ti的含量为0.2％，Fe为余量；所述百分比为质量百分比；
    或者，所述R-T-B系烧结磁体，其包含：Nd的含量为31.5％，B的含量为0.92％，Co的含量为0.5％；Al的含量为1.0％，Cu的含量为0.5％，Ga的含量为0.455％，Ti的含量为0.2％，Fe为余量；所述百分比为质量百分比；
    或者，所述R-T-B系烧结磁体，其包含：Nd的含量为31.5％，Dy的含量为0.5％；B的含量为0.915％，Co的含量为0.5％；Al的含量为0.7％，Cu的含量为0.55％，Ga的含量为0.455％，Ti的含量为0.25％，Fe为余量；所述百分比为质量百分比；
    或者，所述R-T-B系烧结磁体，其包含：Nd的含量为30.2％，B的含量为0.93％，Co的含量为1.5％；Al的含量为0.65％，Cu的含量为0.4％，Ga的含量为0.3％，Ti的含量为0.15％，Fe为余量；所述百分比为质量百分比；
    或者，所述R-T-B系烧结磁体，其包含：Nd的含量为33％，B的含量为0.86％，Co的含量为3.0％；Al的含量为0.8％，Cu的含量为0.36％，Ga的含量为0.4％，Ti的含量为0.05％，Fe为余量；所述百分比为质量百分比。
  5. 一种R-T-B系烧结磁体，其特征在于，其包含主相和晶界相；其中，所述主相包含R 2T 14B，所述晶界相包含R x-(Cu a-Ga b-Al c) y和稀土氧化相；
    其中，x/y＝1.5～3；a/b＝2～5；(a+b)/c＝30～70；
    所述主相的含量为94～98％；所述R x-(Cu a-Ga b-Al c) y的含量为1～3.5％；所述稀土氧化相的含量为1～2.5％，所述百分比为体积百分比。
  6. 如权利要求5所述的R-T-B系烧结磁体，其特征在于，所述晶界相R x-(Cu a-Ga b-Al c) y中，x/y＝1.5～3，a:b:c＝(10～40):(6～19):1。
  7. 一种如权利要求1～4任一项所述的R-T-B系烧结磁体的制备方法，其特征在于，其步骤包括：将R-T-B系烧结磁体的原料依次进行熔炼、铸造、氢破、气流磨、成型、烧结和时效，即可。
  8. 如权利要求7所述的制备方法，其特征在于，所述熔炼为在高频真空熔炼炉中进行；
    较佳地，所述熔炼炉的真空度小于0.1Pa；
    更佳地，所述熔炼炉的真空度小于0.02Pa；
    和/或，所述熔炼的温度为1450～1550℃；
    较佳地，所述熔炼的温度为1500～1550℃；
    和/或，所述铸造在Ar气氛条件下进行；
    和/或，所述铸造的气氛压力为20～70kPa；
    较佳地，所述铸造的气氛压力为30～50kPa；
    和/或，所述铸造的铜辊转速为0.4～2m/s，例如为1m/s；
    和/或，所述铸造得到的R-T-B合金铸片的厚度为0.15～0.5mm；
    较佳地，所述铸造得到的R-T-B合金铸片的厚度为0.2～0.35mm，例如为0.25mm；
    和/或，所述氢破的吸氢温度为20～300℃，例如为25℃；
    和/或，所述氢破的吸氢压力为0.12～0.19MPa，例如为0.19MPa；
    和/或，所述氢破的脱氢时间为0.5～5h，例如为2h；
    和/或，所述氢破的脱氢温度为450～600℃，例如为550℃；
    和/或，所述气流磨为将所述R-T-B合金粉体送入气流磨机进行气流磨继续破碎，得到细粉；
    较佳地，所述细粉的中值粒径D50为3～5.5μm，例如为4μm；
    较佳地，所述气流磨的研磨压力为0.3～0.5MPa，例如为0.4MPa；
    和/或，所述成型在1.8T以上的，例如为1.8T的磁场强度和氮气气氛保护下进行；
    和/或，所述烧结分为四步：(1)升高温度至150～300℃，保温时间为1～4h；(2)升高温度至400～600℃，保温时间为1～4h；(3)升高温度至800～900℃，保温时间为1～4h；(4)升高温度至1000～1090℃，保温时间大于3h；
    所述时效包含一级时效和二级时效；
    较佳地，所述一级时效的温度为850℃～950℃，例如为900℃；
    较佳地，所述二级时效温度为440℃～540℃，例如为480℃。
  9. 一种R-T-B系烧结磁体，其特征在于，其由如权利要求7～8任一项所述的制备方法制备得到。
  10. 一种如权利要求1～6任一项所述的R-T-B系烧结磁体在电机中作为电机转子磁钢的应用。
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