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Xi Jinping, China’s president, may have deliberately revealed how he plans to strike back at the US in the trade war by taking a trip to a magnet factory in eastern China on Monday.
Xi visited the JL MAG Rare-Earth factory in Ganzhou, where he learned about the “production process and operation” of the company, which specializes in magnetic rare-earth elements, “as well as the development of the rare-earth industry,” the state-run Xinhua news agency reported.
Click link for full story: https://www.businessinsider.com/trade-war-xi-jinping-rare-earth-factory-hint-cripple-us-tech-military-2019-5
Cerium in high-energy magnets
The need to develop cerium-containing alloy is growing in importance, not least because of the substantial benefits the technology offers in terms of production, cost and engineering.
Typically, bastnasite rare earth ores in nature contain 49% cerium (CE), while in monozite deposits, one can expect to find approximately 46% Ce, as detailed in Table 1. Praseodymium (Pr) and Neodymium (Nd) are generally found in twin form in nature, and the combination of these two elements is referred to as didymium (‘di’ means two in Greek, and the names of both elements end with ‘dymium’). Modern high-energy permanent magnets tend to be of a didymium iron boron makeup rather than pure neodymium iron boron.
It is clear that cerium accounts for up to 49% of naturally occurring rare earths, but final high- energy permanent magnets do not contain any cerium at all. So how can cerium be used and what are unit magnetic properties of cerium- containing alloys?
Cerium is more plentiful in terms of availability and is cheaper than neodymium and praseodymium. It is also much cheaper than dysprosium and terbium. The study of cerium- containing alloy is not, however, new. Wallace, Craig and Schaller of the University of Pittsburg looked at the anisotropy of Ce2Co17-xFex as early as July 1972, and discovered that Ce2Fe17 alloy did have c-axis anisotropy while Ce2Co17 had basal- plane type anisotropy. Yet despite this, the anisotropy of the alloy was not conducive to making a high enough coercive force.
The use of cerium in high-energy permanent magnets began in early 1970s when Karl Joseph Strnat (generally considered the father of modern rare earth-transition metal permanent magnets), indicated in his 1976 paper for Dayton University, that Vogel and his colleagues had published the first phase diagram for CeCo5 in 1947.
Buschow and his team studied the change in anisotropy of SmCo5-CeCo5 as a function of
22 TECHNOLOGY INTERNATIONAL 2014
Most Magnet Manufacturers today purchase their alloys from organizations that are equipped siMply to Melt various grades of alloys. their charter is not to supply actual Magnets. to expand their business they Must not lose sight of the need for rare earth Magnets with less robust unit Magnetic properties, at a reasonable cost, using rare earth elements that are More abundant
temperature in mid-1975. By that time, Martin Wells and Dev Ratnam of the Crucible Research Center had produced and documented the manufacturing process for making misch-metal cobalt (MMCo5) magnets. Misch-metal is a naturally occurring ore that contains effectively all the rare elements in combined form. The MMCo5 magnets were made using a natural stream of bastnasite-type rare earths with a host of other light and heavy rare earths including lanthanum (La), mixed to the proper stoichiometric ratio of one to five between rare earth and cobalt. Later Ratnam and Wells varied the content of cerium to achieve a magnet with marketable unit magnetic properties. Nevertheless, the Crucible Research Center soon abandoned the practice of making cerium-containing alloys, for the simple reason
that because the cost of the raw material was only a tiny fraction of the total manufacturing cost (small magnets and highly labor intensive), the final production cost would not be very different between samarium-based magnets and MMCo5 magnets. The lack of repeatability of the magnetic properties from one batch to another, as well as from one part to another part, was a secondary reason for stopping the program in its entirety.
DL Martin of the General Electric Research Center (Schenectady, NY) produced a cerium containing alloy of Sm1-xMMxCo5, with energy capacity of 14.5-18.0MGOe, where x ranged between 0 and 0.4. The magnets exhibited an intrinsic coercivity ranging up to 24kOe. The lack of repeatability of magnetic properties between
material lots, as well as the small difference in terms of the selling price of MMCo5 and SmCo5 magnets, damped the enthusiasm of magnetic circuit designers around the world and therefore magnet manufacturers abandoned the practice for more than a decade.
KHJ Buschow of Philips Research Laboratories determined that the magnetic properties of several compounds of RCo5 (cerium and samarium) are strongly related to magnetocrystalline anisotropy (Figure 1). When Buschow studied the characteristics of the CeCo5 system, cerium was considered a rare earth element with potentially high anisotropy when combined with transition metals such as iron and cobalt.
Cerium in NdFeB alloys
In 1985 M Okada and M Homma of Tohoku University in Sendai, Japan, observed the process of making pure rare earth alloys by using a rare ore containing 49% Ce and a host of other light and heavy rare earth oxides. The separation of pure Nd and pure Pr was more complex, and therefore very expensive. Figure 1 shows the typical process of generating pure Nd and Pr.
Rare earth ore typically has a host of light and heavy rare earths. The extraneous elements are removed as the first order of priority and then La has to be removed in its entirety. Leaving a small percentage of Ce would reduce the cost of the processing substantially, especially as bringing the content of Ce down to almost zero in the alloys will need many more expensive steps. Nevertheless,
the remaining Ce content will reduce the intrinsic coercive force of the alloy and this reduction will be proportional to how much is left in the final alloy.
Making didymium the base alloy
To determine the effect of cerium on rare earth iron boron magnets, Okada and Homma selected three Ce-containing alloys with the following compositions:
NdFeB alloy with no cerium-Nd – 10%wt Pr
NdFeB alloy with 5% cerium-Nd – 15%wt Pr, 5% Ce (5Ce-didymium)
NdFeB alloy with 40% cerium-Nd – 10%wt Pr,
40% Ce (40Ce-didymium)
The range of the unit magnetic properties achieved with the above Ce-containing alloys ranged from from 27-40MGOe with various values of the intrinsic coercive force depending on the content of Ce-didymium. It is important to note that the alloys were made using an induction vacuum melt process, crushed into 258µm (average) particle size, and ball milled to a 3-4µm average particle size with the oxygen content being substantially higher than with the modern
Figure 1: Anistrophy in SmC05
methods of manufacturing. In other words, the vacuum-melted buttons may have had some inhomogeneity across their depth and thus the microstructure may have been less conducive to making high magnetic properties. Despite this, the result of the process was immensely encouraging and the future seemed to be very promising for ceruim containing alloys. A typical NdFeB alloy today is made of strip cast alloy that is subsequently hydrogen-decrepitated and jet milled with a much lower oxygen content and much improved particle distribution. As a
result, enhanced unit magnetic properties have been realized.
One important observation that can be drawn is that the distribution of Ce and Nd in this alloy is impressively even, but the distribution becomes uneven as the content of Ce increases and the magnetic properties deteriorate.
Manufacturing of cerium
A modern approach to producing Ce-didymium permanent magnets includes strip casting the
alloy; hydrogen decrepitation of the alloy; jet milling to an average of 3µm particle size with a reasonable Gaussian distribution; hydrostatically
The saturation magnetization of 13.7kG for the Ce-didymium alloy is far lower than that of the didymium base alloy. Furthermore, the curie temperature of the modified alloy could be as much as 15-20°C lower than the didymium alloy.
The didymium alloy exhibits a curie point of around
310°C. However there are applications in use today – as well as potential future examples – where the intrinsic coercive force of the modified alloy will be more than sufficient. Figure 2 shows the relationship between a typical NdFeB magnet and a Ce-didymium magnet produced using the above manufacturing steps.
Most magnet manufacturers today purchase their alloys from organizations that are equipped simply to melt various grades of alloys. Their charter is not to supply actual magnets. To expand their business they must not lose sight of the fact that there is a need for rare earth magnets with
less robust unit magnetic properties, at a reasonable cost, using rare earth elements that are more abundant.
They will need to develop Ce-containing alloy to essentially accomplish two goals: first, to maintain the cost of the rare earth alloys at a price level where it will not choke the current and future use of these magnets in applications
where super high-magnetic characteristics may not be needed; second, to use the most abundant rare earth element and help ensure the proper usage balance between the heavy and light rare earths.
pressing at a magnetic field of 20kOe, and subsequently cold iso-statically pressing the part; and sintering at a temperature of around 1,020°C and annealing at 520°C.
These key manufacturing steps apply to an alloy of generic form, such as (Nd1-xCex)30FebalanceB1.0 with X being 0, 0.1, 0.15 and 0.2. The best result was achieved for X=0.2, with unit magnet properties of Br = 13.7kG, Hci of 12.0kOe and BHmax of
41.0MGOe. The pure Ce-based alloy with the C2Fe14B structure will have a much lower Br and intrinsic coercive force and therefore a lower energy product. This is because the magnetic moment and the anisotropy of Ce2Fe14B are lower than Ce-enriched alloy, as well as being much lower than the pure NdFe14B alloy.
The important factor in achieving a high Br and a higher density magnet has been the use of a dual
component alloy. Ce2Fe14 alloy has very low anisotropy of less than 40kOe, while Ce-enriched didymium alloy will achieve a high densification at a low temperature of around 1,020°C.
Figure 2: Schematic illustration of extraction process of the rare earth elements from ore
Karl Joseph Strnat: Introduction to the Workshop, Rare Earth Cobalt Permanent Magnet And Their Applications, Dayton, June,1976
Karl Joseph Strnat: Review of Rare Earth Magnets, Rare Earth
Cobalt Permanent Magnets And Their Applications, June 1976
Ratnam, DV, and Wells, MGH, AIP Conference Proc.N0.18 Part 2, p1154 (1974)
HG Schaller, RS Craig and WE Wallace, J.Appl.Phys. Vol.143, No.7
H Domazer: New Substituted SmCo, Workshop Rare Earth Cobalt, June 1976
M Okada, M Homma: The Properties and Microstructure of
Ce-Didymium, International Workshop on Rare Earth Magnets, May 1985, Dayton
Crucible Research Center/Crucible Magnetics; private notes and studies of MMCO5 trial runs and manufacturing procedure
Panchnathanl Viswanathan: US Patent 6261387, Magnequench
DL Martin and MG Benz, Cobalt Rare Earth Permanent Magnet Alloys, International Conference on Magnetism, Grenoble, France, September 1970
AM Diepen and KHJ Buschow, Philips Research Laboratories, Eindhoven, The Netherlands,The Origin of High Uniaxial Magnetocrystalline Anisotropy of SmCo5, 1975
Haibo Feng, Anhua Li, Jingdai Wang, Shulin Huag, Minggang Zu
and Wei Li, Fabrication of High performance NdCe-containing magnets, International Workshop on Rare Magnets and their Applications,September 2012, Nagasaki, Japan
New methods leading to the reduction of heavy rare-earth elements in NdFeB permanent magnets with enhanced coercive force are being implemented by magnet manufacturers
The advent of rare earth-transition metal alloys, or inter-metallic compounds, such as samarium cobalt and a ternary system composed of neodymium iron and boron (NdFeB) permanent magnets revolutionized the usage of permanent magnets. The latter alloys (Figure 1) with their extremely high coercive forces and substantially higher energy products (as compared with their predecessor systems, alnico and ceramic) not only simplified the design of magnetic circuits, but made possible the miniaturization of a vast array of magnetic devices. Nevertheless, the lower Curie temperature of this alloy has made it prone to loss of coercive force (Hci) at higher operating temperatures.
There has been a constant improvement in coercivity of NdFeB magnets since their inception. Figure 2 shows the latter improvement. Increase in demand for NdFeB magnets coupled with a relative shortage of heavy rare earths (HRE) such as dysprosium (Dy) and terbium (Tb) has persuaded magnet manufacturers to price the alloy, among other factors, as a function of the content of HRE, causing fear, uncertainty and skepticism among magnetic device designers and manufacturers. This was the genesis of the decision by magnet manufacturers to launch an orchestrated attempt to reduce the content of HREs or partially replace the latter rare earths,
with more abundant and less used HREs such as holmium and others.
Light rare earths couple ferromagnetically with transition metals, resulting in higher saturation magnetization. NdFeB, with its high saturation magnetization and extremely high-energy product, does have a drawback. That is, the coercive force of this alloy system suffers exponentially as the operating temperature of the magnet increases.
Figure 1: The coercive forces of rare earth-transition metal alloys and inter-metallic compounds are increasing faster than previously
To remedy this situation selectively, a portion of Nd (light rare earth or LRE) is replaced by HRE (Figure3). Although HREs coupling with transition metals ferromagnetically produces a somewhat lower saturation magnetization, it does increase the anisotropy field of the alloy and therefore increases the intrinsic coercive force (Hci) of the magnet. The degree of enhancement of Hci is a function of the content of HRE. The higher the content of HRE, the higher the coercive force will be. However, there is an upper limit beyond which the coercive force starts to show a gradual decline.
Strip casting technology was a much more powerful tool affecting the efficiency and quality of NdFeB magnets than any other changes since the inception of manufacturing of sintered Nd magnets. It is prudent to observe that the
transition from the classical book mold and cup cake (ingot melting) process to strip casting hasimproved the efficiency of usage of HREs (which are associated with higher vapor pressure and excessive loss of HREs in the melting process) to a great extent.
Figure 2: The steady improvement in coercive force of NdFeB magnets since their inception
Strip casting is another term for rapid quenching process or centrifugal casting. This process produces thin strips of alloy (as opposed to that produced by ingot casting) by dropping the molten alloy on a single or twin rollers rotating at high speed, causing the molten alloy to solidify to a thickness of 0.03mm to perhaps as thick as 4-5mm. The strips used for production have been in a narrow range of thicker than 0.1mm and thinner than 0.3mm. Strips of solidified alloy exhibit a columnar crystal that grows from the surface of the roller in the direction of thickness of the strip.
The remarkable improvement in the microstructure of the rapidly solidified NdFeB strips (columnar structure of hard magnetic grain) greatly enhances the homogeneity and the unit properties of the magnet produced from the strip cast material.
Strip cast of NdFeB type composition, containing niobium (Nb) or molybdenum (Mo) in the range of one atomic weight percent, has considerably improved the coercive force of this alloy without a substantial loss in the in (Br).
Without the advent of rapidly solidified strip casting of NdFe magnets, the current degree of improvement in the use of HREs would have been virtually impossible. Figures 4 and 5 show the effect of Nb on Hci and Br. Figure 6 shows the grinding resistance for the sintered NdFeB magnet as a function of the content of Nb – the higher level of Nb significantly increases the resistance to grinding. Therefore, there is a limit as to how much Nb can be added to the alloy.
Figure 3: A portion of Nd (light rare earth or LRE) replaced by HRE to counter the detrimental effects of increased operating temperatures
Figure 4: The effect of niobium on the intrinsic coercive force and residual induction of NdFeB magnets using strip casting
and ingot casting technology
One successful method of enhancing the coercive force of NdFeB magnets is to diffuse dysprosium into the grain boundary of an alloy made of Nd, Fe, B (no heavy rare-earth elements) either in the form of strip-cast or finished magnets.
The crystal anisotropy of the magnetic grains surface region is always lower than that of the inside of the grains, as this region suffers defects and is under stress.
The principle of grain boundary diffusion is based on the premise that when a reverse magnetic field is applied to a magnet, magnetization reversal happens to all particles making up the mass of the magnet. The latter reversal starts from those particles that nestle on the surface of the particles. If the concentration of dysprosium (high anisotropy heavy RE) is increased on the surface, the magnetization reversal becomes difficult in the particles, thus increasing the coercive force of the magnet. Since the concentration of dysprosium decreases in the central region of the particles, the loss of saturation magnetization, and thus the drop in the Br of the magnet, will not be significant. Although there are no available guidelines as to how much dysprosium can be saved by using grain boundary diffusion, generally this process saves as much as 50% dysprosium used in a typical melt for a given value of coercive force, with very little loss in the value of Br of the magnet. Figure 7 shows the effect of Dy grain boundary diffusion in the strip- cast stage of manufacturing.
Figure 5: The effect of niobium on the intrinsic coercive force and residual induction of NdFeB magnets using strip casting
Figure 6: The grinding resistance for the sintered NdFeB magnet as a function of the content of Nb
Figure 7: The effect of the Dy grain boundary diffusion concept in the strip-cast stage of manufacturing
The concept of grain boundary diffusion started with finished uncoated magnets. In light of the fact that the process consists of a secondary operation, at temperatures exceeding 700ºC, the process was not deemed appropriate for magnets with less favorable aspect ratios (the ratio of the magnet thickness to the magnet surface area). Thinner magnets with a large surface area and small thickness-unfavorable aspect ratio did suffer enough deformation and warping to be classified as rejects. So the process would lend itself only to a select group of geometries. This process may be ideal for applications where the magnet is small and not prone to deformation on account of high temperature exposure.
The alternative method of grain diffusion with which the magnet manufacturing industry has been successful is the Dy grain boundary diffusion of cast strips, and the ultimate manufacturing of the magnets by using the conventional powder metal process.
Quantum size effects have spawned much interest among magnet scientists and technologists. As the size of particles in a nanocomposite structure decreases, there is an increase in the fraction of surface energy (surface atoms), which could lead to a considerably higher energy product in the permanent magnet.
The magnetic properties of magnets made from nanoparticles, among other factors, is a function of the chemical composition, the microstructure, the size and the shape of the particle, the crystal lattice and the morphology of particles. Controlling the latter parameters within a given range in the process of synthesis of nanomaterial will be, if not impossible, very difficult. Therefore, the properties of nanomaterial of the same type will be significantly different. The majority of the current high-energy magnetic alloys are of complex composition. As a result, this causes the range of parameters in the synthesis of nanomaterial to be extremely narrow.
The various processes of synthesis of magnetic nanomaterial also go completely against the principle of maintaining the proper stoichiometric ratio that is necessary in order to achieve sound magnetic properties.
For example, if the stoichiometric ratio of Nd2Fe14B or SmCo5 alloys changes during the synthesis, the resultant phases may be either slightly magnetic or non-magnetic; thus it significantly reduces the unit magnetic properties of the stated alloys.
The synthesis of such nanocomposites may require a manufacturing method that is entirely different from the existing powder metal method of manufacturing. The cost of the magnet is a function of the new manufacturing technology. If the latter cost is too high, the product may not be deemed viable.
The manufacturing of nanocomposite of NdFeB was orginally proposed by a Japanese firm as early as the late 1990s. The firm, in cooperation with a major university in the USA and one in Japan, actually managed to produced a very high- saturation and low-Hci magnet using a unique method of synthesis. Figure 8 shows the second quadrant demagnetization curve of a magnet using a non-powder metal process, a nanocomposite technology. The magnet exhibits sound magnetic properties. Nevertheless, that was the last time it was heard of. The company may have decided to abandon the project for reasons unknown, or it may have become part of a larger firm.
In summary, although the concept of nanocomposites may be a viable method of manufacturing NdFeB magnets, the cost and method of producing high-energy NdFeB magnets may be questionable.
Figure 8: The second quadrant demagnetization curve of a magnet using a non-powder metal process
Temperature control methods Magnetic circuit designers and final device engineers have used their imaginations to design mechanisms that control the working temperature of the device, making the magnet less prone to high-temperature exposure. This supplementary device may take the form of a cooling device external to the magnet or any other temperature- control mechanism that will essentially perform the latter task.
There are many existing and new methods
being developed where magnet manufacturers are reducing the use of HRE elements. There is also
an intensive effort being launched to eliminate the use of the latter family of elements altogether. n
1) Yukata Matsuura: Current Status of NdFeB Magnets In
Japan- China Magnetics Shanghai, September 2006, China
2) Karl J Strnat, Herb Mildrum,T.K.Tan –Sintered NdFeB magnets Modified with Holmium and Cobalt- “The Tenth International Workshop pm Rare Earth Magnets May 1989
3) Private dialogs with Matsuura in reference to Grain Boundary
Diffusion of Dysprosium
4) Naoko Ono, Massato Sagawa, R.Kasada” Production of High Performance Magnets by Grain Boundary Diffusion, Journal of Magnetics and Magnetism, February 2011
5) Hongwang Zhang,Shen Peng, Shuan-bing Rong,J.Ping Liu, Ying
Zhang,M.J.Kramer,Journal ,of Material Chemistry June 6th
6) Magnetic Nanocomposite Materials for High Temperature Applications- Frank Johnson, Amy Hsio,ColinAshe, David Laughlin, David Lambeth, Michael McHenry- Carnegie Mellon University and Lajors K. Varga ,Hungarian Academy of Sciences, Budapest, Hungary
7) S P Gubin, Yu A Koksharov,G.B.Khomutov,G Yu Yurkov, Russian
Chemical Reviews 2005
8) Shuk Rashidi, Use and Reduction and Probable Remedies of Heavy Rare Earths in Proceedings of the International Workshop on Technology and Economics of Rare Earths and Metals – 2011
9) Shuk Rashidi, Global Magnet Market: NdFeB Price Escalation and Revised Manufacturing Paradigm- China Magnetics Conference 2007 Beijing China
10) Optimization of the Geometry of Strip Cast NdFeB Alloy – Beijing Zhone Ke San Huan High Tech Ltd- private communication
Abstract—The advent of NdFeB permanent magnets ushered in a slate of new applications that were virtually impossible with the existing families of permanent magnet alloys.The lower Curie Temperatures and the associated thermal magnetization losses of Br and Hci, made the use of NdFeB magnets difficult if not down right impossible- in host of high temperature devices.To enhance the anisotropy field of this family of alloys, a portion of light rare earths was replaced by heavy rare earth metals. The latter enhancement was accompanied by some loss of remanence and the problems of a poor balance between the heavy and light rare earth metals. This paper addresses the benefits and the problems associated with the heavy rare earths and the potential attempts to reduce and or avoid the dependence on heavy rare earths wherever and whenever possible.
Up until 1983, SmCo5 and Sm2Co17 made up the bulk of magnets used in miniature, high performance devices, ranging from computer disk drives to a host of factory automation, office automation and automotive components. The extremely high energy products and the superb Curie Temperatures of the latter alloys ushered in a host of new applications which were virtually impossible with other existing families of permanent magnets. The cobalt crisis of 1977, when the Katangese rebels invaded Zaire and flooded the cobalt mines and causing the price of cobalt to escalate to better than US$ 40.00/lb from a low of US$ 4.00/lb – in the gray market, instilled fear in the minds of many manufacturers, not to mention the magnet users. The magnet laboratories through out the industrialized nations started looking at different families of hard magnetic alloys, in quest of inventing, a system or systems of alloys that were not at the mercy of sources of supply raw materials, some of which were in politically and economically unstable regions of the world.
This was the genesis of Neodymium Iron Boron (NdFeB) magnets. In 1983, John Croat of GM and Sagawa of Sumitomo Specialty Metals Corporation invented the so- called MQ ( Magnequench) and sintered NdFeB permanent magnets, almost concurrently. In Fig(1), Yukata Matsuura of Neomax depicts the increasing trend in the energy product of NdFeB alloys.
Figure 1. Transition of world record energy product
The evolution of the NdFeB seemed to have a few more complications than that of its predecessors SmCo5 and Sm2Co17 systems of alloys. The lower Curie Temperature (around 315 degree centigrade), the magnet being prone to corrosion, coupled with lower thermal stability, were some of the unique undesirable characteristics, that for better or for worse separated this alloy from the Sm-Co families of permanent magnets.
The material scientists responsible for the invention of Nd based rare earth transition metal alloys did what any typical inventor does. They based their technology of the manufacturing of the new system of alloys, on an existing process that had proven effective and had been around for years. In this case, most of the manufacturing events were primarily based on the technology of powder metal process used for making Sm-Co.
Unfortunately, there were some vast differences between the two alloys. In the early days of Nd magnets it was not uncommon to prepare an alloy with a composition slightly richer in Nd as it was done with the SmCo alloys. None the less, an excess amount of Nd increased the level of Nd – rich phase in the grain boundary, which in turn made the magnet more prone to corrosion.
The second challenge for the manufacturer and for the end user was the fact that the magnet exhibited a much lower Curie temperature leading to higher reversible and irreversible temperature coefficient of induction and coercive forces. The end user did not have the luxury of taking the magnet to a high temperature and yet expect the device to perform as though the magnets were Sm based. So effectively we had a new family of permanent magnets that had room temperature characteristics of SmCo and yet the Curie temperature was even lower than that exhibited by hard ferrites.
The industry launched a systematic study to improve the unit magnetic properties of the Nd based magnets, thru the implementation of a host of process changes, and changes in the microstructure of the alloy. The lower Curie Temperature of NdFeB magnets is responsible for its higher reversible coefficient. Cobalt was added to increase the Curie temperature. But Cobalt does tend to reduce the anisotropy therefore the intrinsic coercive force, if the level of Cobalt exceeds a certain level. The latter limit is indicated to be around 10%. The coercivity of NdFeB magnets in practice amounts to no more than 20 to 40% of the theoretical limits. Sagawa and coworkers discovered that replacement of a portion of Nd by Dysprosium would enhance the anisotropy of Nd based alloy and thus increase the intrinsic coercive force. Immediately following Sagawa, Ghandahari and Fidler discovered that using Dy2O3 as a sintering additive also had a similar result. The latter was a low cost approach to the enhancement of the Nd based alloy. The addition of DY2O3, however, did introduce a much higher content of oxygen into the alloy (oxide causes decrease in the remanence and possibly provides easy nucleation sites for nucleation of domain walls) exhibited less homogeneous distribution of Dy into 2-14-1 grains. The practice of adding Dy became a more bona fide method for increasing the anisotropy of the alloy. Fig (2) shows the effect of Dysprosium on Br and Hci. Fig (3) is trend curve for the enhancement of Hci between 1980 and 2005.
Figure 2. The effect of Dysprosium on Br and Hci
Figure 3. Improvement of Nd-Fe-B sintered magnet coercive force
Thereafter, Dysprosium and Terbium (Dy and Tb) were added to increase the intrinsic coercive force. The latter did result in higher cost for the alloys and a partial loss of induction, as the heavy rare earths couple ferri- magnetically with transition metal and thus reduce the saturation magnetization. The accepted, typical rule was that for adding one percent of heavy rare earth, the intrinsic coercive force of the alloy will enhance by better than 1.5 Kilo Oersted. The important finding of use of Dy was the fact that up to 10% replacement of total rare earth, by Dy did result in increase in the intrinsic coercive force, beyond which there is a strong deviation from linearity. The doping of non- rare earth metals did show some promise of increasing the intrinsic coercive force. Use of metals such as Aluminum and Niobium may enhance the intrinsic coercive force to some extent as well. J.K.Chen and G.Thomas made two alloys where in one a portion of Iron was replaced by Aluminum while in the second alloy a percentage of Boron was replaced by Aluminum. Both showed a marked increase in the intrinsic coercive force with unfortunately higher than 4% decrease in the value of remanence.
The advent of “strip cast” process versus the “ingot cast” (cupcake or book mold type casting), allowed to make alloys with higher homogeneity and far better microstructure – another reason for greater improvement in the unit magnetic properties.
The above improvement made possible, the use of NdFeB in many new devices specially those that required exposure to higher temperatures and higher demagnetizing forces. The NdFeB magnet users and manufacturers therefore fell heavily for magnets using progressively more and more heavy rare elements, as the end users designed their magnetic circuits, conservatively, around alloys which may had much higher coercive force than they really required. The cost of the heavy additive was reasonable enough to justify such change.
The manufacturers decided to adopt a series of grade designations, where the last two letters of the alloy effectively indicated the nominal content of Nd, Dy and Tb. These were designated for example as N35, N38H, N38SH and N38UH, N35EH and etc. So a N38H alloy had a nominal Br of o 12.4 KGauss, and nominal Hci of 17 K Oersted, and supplied by most of the world class suppliers with essentially the same nominal unit magnetic properties. The content of the heavy rare earths typically varied from manufacture to manufacture by 0.5% or thereabouts.
While magnets of the same grade designation may be manufactured by different manufacturers, exhibiting essentially equivalent room temperature properties, the high temperature performance may vary from manufacture to manufacture as the technology of processing may not be of the same level of sophistication. Less technology savvy manufacturers of NdFeB magnets may have used a higher level of HREs in their alloy in an attempt to level the playing field of the magnetic performance, at higher temperatures.
This move, while may have been a good remedy, did seed some problems, both for the magnet suppliers as well as for the magnet users.
Since the premium for the use of HREs was very small, the conservative designer may have used alloys with much higher intrinsic coercive force than he actually needed. In some cases the designer specified the knee of the magnet (at higher temperatures) clear in the third quarter of the magnetization curve. In other words some designer pushed the use of HREs to levels that ultimately became very expensive if not down right impossible. Some designers decided to go away from free Dy alloy to one with some Dy by content, by redesigning the magnetic circuit with thinner magnet, which allowed him (or her) the use of larger air-gap and less problems associated with mechanical dimensioning.
To usher in a semblance of order in the mining, usage and export of rare earths, the Chinese government changes the rules. The changes had a gradually increasing effect on the prices of rare earths across the board, while the HREs felt the effect more intensely as the fear of “balance” took a new dimension.In a nut shell, in the following five and one half years, the price of Nd metal went to higher than 700,000 RMB/ton, from a low of 45,000 RMB/ton, while Dy increased from 500 RMB/Kg ( or thereabouts) to 4,000 RMB/Kg – at the end of the first quarter of 2011.
Fig (4 a) and Fig (4b) shows the change in the price of Nd during the last decade.
Figure 4. The change in the price of Nd during the last decade
The designer was presented with three choices that could potentially solve his problem of not to cope with the thermal problems in his design.
(1) Use a thicker magnet – no expensive heavy rare earths.
(2) Design the system with much smaller air gap and move the operating point to much higher load line.
(3) Use a magnet replacing part of Nd with Dy or Tb at the expense of some sacrifice in the value of air gap flux or air gap flux density and risk the probability of not being able to buy heavy rare earths at all at some point in the future.
Fig (5) is Modified Operation load line and change of alloy.
Figure 5. Modified operation load line and change of alloy
Choice No.1 would mean use of larger device and larger foot print, Choice No.2 would make the cost of non- magnet portion of the circuit more expensive. Therefore choice no.3 was the most logical one to him. Un be-known to him and the magnet supplier the prices of Nd, and Dy would escalate from a low of 45,000 RMB /ton to high of better than 650,000 RMB /ton between year 2004 to 2011, with Dysprosium going thru the same multiple of price increases in China.
The word “balance” was used to point out the lop-sided ratio of light rare earths to heavy rare earths. This was an area of concern as for every 1700 pounds of Nd Oxide, they could produce only one pound of Dysprosium Oxide, in a typical Chinese Bastnasite deposit, while this ratio was around 25 times in the Chinese ionic ore. The ratio of Terbium Oxide to that of Nd oxide was even less favorable. Fig ( 6A ).
Figure 6A. The ratio of Terbium Oxide to Nd Oxide
Chinese rare deposits happen to have a healthy of dose of HREs. The next known largest rare earth deposit in Mountain Pass California, now owned by Moly Corp has virtually no HREs, while there is no public report about the content of HREs the central Asian rare earth deposits.
So there could be better incentive than very higher prices generally for rare earth metals, compounded by limited availability of HREs. We see a concerted effort among the US end users to reduce the use HREs to an absolute minimum or purge such usage all together if possible.
Fig.(6B) shows the estimated supply of rare earth elements from known sources as of March 2010.
Figure 6B. The estimated supply of rare-earth elements from known sources as of March 2010
(1) They are designing new devices around Dy or Tb free alloys.
(2) The have grandfathered some of the old designs around alloys with HREs as changing those will be a virtual impossibility.
(3) They are looking at a completely different paradigm of design in that they spend a bit more money on the components (tighter tolerance, higher quality return structure) and use less rare earth of less heavy rare earths.
For example, in some motor applications for instance, the use of NdFeB magnets in hybrid cars, some manufacturers use higher heavy rare content alloy and avoid use of cooling system. In light of the scarcity of heavy rare earths, it may be more logical to incorporate cooling system and avoid use of heavy rare earths.
(4) They specify their operating load line and the operating point of the magnet in the second quadrant curve and let the manufacturer decide what alloy they should use. Generally the designer uses a more conservative view in terms of unit properties, specifying more than required content of HREs. The designer specifies the coordinate fail safe coordinate of the magnet in the third quadrant. The manufacturer may be more prudent and cost conscious suggesting alloys that will meet the designers’ requirement, and not break the bank. See Fig (7) and Fig (7B).
Figure 7. Tridus International KJS associations Model HG-700 V1.1.4
(5) The user may expect more transparency from the manufacturer. They put subtle or not so subtle pressure on the supplier to increase the yield and use more efficient technology to produce higher yield parts. When the cost of raw material quintuples, the user pays a lot more for the inefficiency of the supplier if the supplier is not able to recycle. Fig (8A) and Fig (8B) show the methods suggested, recycling Nd, some seven years ago. Recycling or reclamation is a de-facto method of increasing the yield today. This has become possible in light of the fact that the price of Nd and Dy has increased at least eight folds since 2004.
Figure 8. Recovery of Nd from magnet sludge – using Nd3 hydrolysis
(6) Recycling becomes the mantra of the end user. They persuade the supplier to do the latter and share the return.
(7) Use of Dysprosium Grain Boundary Diffusion (GBD) is a technology that is somewhat promising. Nevertheless the cost of added process to accomplish the latter still needs to come down to make the process economically feasible.
This process does use much lower content of Dy and the magnet can undergo the diffusion process selectively. For example a motor magnet can be diffused only in the area of the arc where it is more prone to the armature reaction.
The effect of (GBD) has much lower effect on reducing the remanence of the magnet. GBD requires a much lower content of heavy rate earth to achieve the same level of coercivity as achieved with Dysprosium used in the melt process. Anecdotally this could be half or less than half of Dysprosium used in conventional cast.
If the purpose of GBD is to reduce the usage of Dysprosium, this process is a bona-fide process. If the goal is to reduce the overall cost of manufacturing, there is some cloud over this issue at this point in time.
 Yukata Matsuura: Current Status of NdFeB Magnets in Japan-China Magneitcs Shanghai, September 2006. China Magnetics , September 19-21, 2006 – Sofitel Hyland Hotel – Shanghai, China
 Y. Matsuura, S. Hirosawa, H. Yamamoto, S. Fujimura and M. Sagawa, “Magnetic Properties of the Nd sub 2 (Fe sub 1–x Co sub x ) sub 14 B System,” Appl.Phys, Vol. 46, no. 3, pp. 308-310, February. 1985
 M. Tokunaga, M. Tobise, N. Meguro, and H. Harada, “Microstructure of R-Fe-B sintered magnet,” IEEE Transactions on Magnetics, vol. 22, no. 5, pp. 904-909, September 1986
 S. F .Cheng, V. K. Shina, Y. Xu, J. M. Elbicki, E. B. Boltich, W. F. Wallace, S. G. Sankar, and D. E. Laughlin, “Magnetic and structural properties of SmTiFe11-xCox alloys,” Journal of Magnetism and Magnetic Materials, vol. 75, no. 3, pp. 330-338, December, 1988.
 J. K. Chen, G. Thomas- Al Substitution in NdFeB Magnets- High Performance Permanent Mag, Mater. Res. Soc. Symp. Proc., vol. 96, 1987.
 M. H. Ghandahari, J. Fidler, “Microstructural evidence for the magnetic surface hardening of Dy2O3-doped Nd15Fe77B8 magnets,” Material Letters, vol. 5, no. 7-8, pp. 285-288, July, 1987.
 Karl J. Strnat, H. Mildrum, T. K. Tran, “Sintered Nd FeB Magnets Modified with Holium and Cobalt,” The 10th International Workshop pm RE Magnets, vol. 1, pp.523, May 1989.
 J.Fedler and K.G.Knoch – The Influence of Dopants on Microstructure and Coercivity of NdFeB Magnets, The Proceedings of the Tenth International Conference on Rare Earth Magnets, 16-19 May 1989.
 Private dialogs with Y.Matsurra – in several conferences re Dysprosium Grain Boundary Diffusion- including during Magnetics 2011, February 28- March 2, 2011, San Antionio Texas , USA
 Naoko Oono, Massato Sagawa, R.Kasada, H.Matsui , “Production of High Performance Sintered NdFeB magnets by Grain Boundary Diffusion Treatment With Dysprosium–Nickel–Aluminum Alloy”,Journal of Magnetics and Magnetism ,Vol.323, no.3-4, pp.297-300, February 2011.
 Shinetsu Rare Earth Magnets – A Commercial Narrative on Grain Boundary Diffusion of Dysprosium – Shinetsu Rare Magnets- A Commercial Data Sheet – printed June 10, 2009.
 Lanthanide Resources and Alternatives- Oakdene Hollins Research & Consulting- A Report for Dept. for Transport and Dept. for Business, Innovation and Skills- March 2010 – UK