CN107610869B - Soft magnetic alloy - Google Patents
Soft magnetic alloy Download PDFInfo
- Publication number
- CN107610869B CN107610869B CN201710562865.0A CN201710562865A CN107610869B CN 107610869 B CN107610869 B CN 107610869B CN 201710562865 A CN201710562865 A CN 201710562865A CN 107610869 B CN107610869 B CN 107610869B
- Authority
- CN
- China
- Prior art keywords
- straight line
- soft magnetic
- magnetic alloy
- point
- mass
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Images
Landscapes
- Soft Magnetic Materials (AREA)
Abstract
The present invention relates to soft magnetic alloys. The invention relates to a soft magnetic alloy comprising: ni and at least one element selected from the group consisting of Al, Si and V, with the balance being Fe and unavoidable impurities, wherein when the content of Ni, and the total content of Al, Si and V are represented by [ Ni ] and [ M ] in mass%, respectively, and the relationship between [ Ni ] and [ M ] is plotted, the coordinates ([ Ni ], [ M ]) exist within the region surrounded by straight lines A, B, C, D and E.
Description
Technical Field
The present invention relates to a soft magnetic alloy, and more particularly, to a soft magnetic iron-based alloy that can obtain a high magnetic flux density.
Background
Soft magnetic materials have been widely used as materials for forming electrical devices such as motors. With the recent trend of size reduction of electrical devices and accompanying increase in current, high magnetic flux density has been required in soft magnetic materials. Further, as the current density increases, the soft magnetic material requires excellent soft magnetic characteristics, i.e., low coercive force and the property that the magnetic flux density does not tend to be saturated, within a region of high magnetic field strength.
For example, if the value of the current flowing in the coil constituting the motor is set to be doubled, the number of turns of the coil can be halved (which is necessary to obtain the same output), so that reduction in size of the motor can be achieved. For this reason, it is necessary that the magnetic flux density of the soft magnetic material forming the iron core is not saturated at a magnetic field strength corresponding to a current value. If the magnetic flux density of the soft magnetic material forming the core can be doubled, the same magnetic flux can be obtained even if the sectional area of the core is halved. Therefore, the size of the motor as a whole can be reduced.
Pure iron is known as a soft magnetic material with a high magnetic flux density. A Permendur alloy (Permendur) which is an Fe — Co system alloy is known as a soft magnetic material having a higher magnetic flux density than pure iron. In addition to the hammered alloy, a soft magnetic alloy containing Co and having a high magnetic flux density is known. For example, patent document 1 discloses an iron-based alloy containing 25.0 mass% or more and less than 30.0 mass% of Co and other additive elements. Further, an electromagnetic steel sheet (silicon steel sheet) which is an iron-based alloy containing Si is known as a representative soft magnetic material.
Patent document 1: JP-A-2006-193779
Disclosure of Invention
In recent years, the residual magnetic flux density (Br) of permanent magnets used in motors has increased. Therefore, the soft magnetic material forming the core or the yoke is also required to follow such a high magnetic flux density, and is required to have a high saturation magnetic flux density. The Fe-Co system alloy represented by the Pyngeid alloy can realize a high magnetic flux density. However, since the content of Co is large, the Fe — Co system alloy is very expensive and has poor workability in many cases. Electromagnetic steel sheets are inexpensive and show relatively high magnetic permeability, but their magnetic flux density is not so high. For example, it is difficult to achieve a magnetic flux density of 1.7T or more for an electromagnetic steel sheet.
The present invention aims to provide a soft magnetic alloy having a high saturation magnetic flux density and being inexpensive.
In order to solve the above problems, the present invention provides a soft magnetic alloy comprising:
ni, and
at least one element selected from the group consisting of Al, Si and V,
the balance being Fe and unavoidable impurities,
wherein when the content of Ni, and the total content of Al, Si and V are represented by [ Ni ] and [ M ] in mass%, respectively, and the relationship between [ Ni ] and [ M ] is plotted, the coordinates ([ Ni ], [ M ]) exist within a region surrounded by the following straight line A, the following straight line B, the following straight line C, the following straight line D and the following straight line E:
a straight line A: [ M ] ═ 0.01;
a straight line B: [ Ni ] ═ 11.0;
a straight line C: a straight line connecting a point ([ Ni ], [ M ]) of (11.0,7.00) and a point ([ Ni ], [ M ]) of (3.0, 10.00);
a straight line D: a straight line connecting a point ([ Ni ], [ M ]) of (3.0,10.00) and a point ([ Ni ], [ M ]) of (0.1, 7.00); and
line E: [ Ni ] ═ 0.1.
Preferably, the coordinates ([ Ni ], [ M ]) are present within a region enclosed by the straight line a, the straight line C, the straight line D, the straight line E, the following straight line F, and the following straight line G:
a straight line F: a straight line connecting a point ([ Ni ], [ M ]) of (1.0,0.01) and a point ([ Ni ], [ M ]) of (6.5, 3.50); and
a straight line G: [ Ni ] ═ 6.5.
In this case, it is more preferable that the coordinates ([ Ni ], [ M ]) are present within a region surrounded by the straight line D, the straight line E, the straight line G, the following straight line H, and the following straight line I:
a straight line H: a straight line connecting a point ([ Ni ], [ M ]) of (0.1,0.50) and a point ([ Ni ], [ M ]) of (6.5, 3.50); and
a straight line I: and a straight line connecting a point ([ Ni ], [ M ]) of (6.5,7.00) and a point ([ Ni ], [ M ]) of (3.0, 10.00).
The soft magnetic alloy may further include, in mass%:
1％≤Cr≤14％。
the soft magnetic alloy may further include, in mass%:
1％≤Mo≤6％。
in this case, the soft magnetic alloy may further contain Cr and Mo, and 1% or more and 3.3% or less by mass of Cr and 3.3Mo and 14% or less are satisfied.
The soft magnetic alloy may further contain at least one element selected from the group consisting of:
0.03％≤Pb≤0.30％，
0.002％≤Bi≤0.020％，
0.002％≤Ca≤0.20％，
te is 0.01% or more and 0.20% or less, and
0.03％≤Se≤0.30％。
the soft magnetic alloy preferably has a Vickers hardness (Vickers hardness) Hv of 250 or more.
The soft magnetic alloy according to the present invention has the following composition (component composition): the coordinates ([ Ni ], [ M ]) fall within a region surrounded by straight lines A to E in the [ Ni ] - [ M ] coordinate system, and thus have such a high saturation magnetic flux density of 1.7T or more. At the same time, such a low coercive force of 1,000A/m or less can be achieved. Therefore, an excellent soft magnetic alloy having both a high saturation magnetic flux density and a low coercive force can be obtained. Since the composition does not contain many expensive additive elements such as Co, the soft magnetic alloy can be produced inexpensively.
Here, in the case where the soft magnetic alloy has a composition whose coordinates ([ Ni ], [ M ]) fall within the region surrounded by the straight line A, C, D, E, F and G, a low coercive force is easily achieved.
In this case, in the case where the soft magnetic alloy has a composition whose coordinates ([ Ni ], [ M ]) fall within the region surrounded by the straight lines D, E, G, H and I, a lower coercive force is more easily achieved.
In the case where the soft magnetic alloy contains Cr and/or Mo in the above-described amounts, a soft magnetic alloy having high electric resistance and high corrosion resistance in addition to low coercive force and high saturation magnetic flux density can be obtained.
In the case where the soft magnetic alloy contains at least one element selected from the group consisting of Pb, Bi, Ca, Te, and Se in the above amount, the machinability (machinability) of the soft magnetic alloy can be advantageously improved.
In the case where the vickers hardness Hv of the soft magnetic alloy is 250 or more, the strength as a material and the excellent soft magnetic characteristics can be simultaneously realized.
Drawings
Fig. 1 is a graph plotting the content of Ni in the soft magnetic alloy according to the embodiment of the present invention against the total content of Al, Si, and V.
Detailed Description
Hereinafter, the soft magnetic alloy according to an embodiment of the present invention will be described in detail.
(general of Soft magnetic alloy)
The soft magnetic alloy according to an embodiment of the present invention contains the following elements and the balance consisting of Fe and inevitable impurities:
ni; and
at least one element selected from the group consisting of Al, Si and V (hereinafter may be referred to as "Al and the like").
The content of Ni, and the total content of Al and the like exist within a predetermined region which will be described later.
The soft magnetic alloy according to the embodiment of the present invention may optionally contain at least one of Cr and Mo in addition to the essential elements Ni and Al, etc. Further, the soft magnetic alloy according to the embodiment of the present invention may optionally contain at least one element selected from the group consisting of Pb, Bi, Ca, Te, and Se in addition to the essential elements Ni and Al, etc., and further in addition to at least one of Cr and Mo. Preferred contents of each of the above elements will be described below.
It is allowed to contain inevitable impurities within a range not to impair the magnetic or electrical characteristics of the soft magnetic alloy. Specific examples of the inevitable impurities include, in mass%:
C≤0.04％，
Mn≤0.3％，
P≤0.06％，
S≤0.06％，
N≤0.06％，
Cu≤0.1％，
co < 0.06%, and
O≤1％。
the soft magnetic alloy according to an embodiment of the present invention may be produced in the following manner: each component metal is smelted (smelt), and then rolling, forging, and the like are appropriately performed. A heat treatment such as magnetic annealing may be performed. Examples of temperatures during magnetic annealing may include temperatures from 800 ℃ to 1200 ℃.
(composition of ingredients within the first region)
In the soft magnetic alloy according to the embodiment of the present invention, the content of Ni, and the total content of Al and the like have a predetermined relationship. Specifically, when the content of Ni is represented by [ Ni ], and the total content of Al and the like (i.e., the total content of Al, Si, and V) is represented by [ M ], and the relationship between [ Ni ] and [ M ] is plotted, the [ Ni ] and [ M ] exist within a predetermined first region. In this specification, the content of each of the elements including Ni, Al, and the like is expressed in units of mass%. The term "within" in each region includes points and vertices on the boundary line of the defined region.
FIG. 1 is a graph plotting [ Ni ] and [ M ]. Here, the first region is defined as a pentagonal region surrounded by a straight line a, a straight line B, a straight line C, a straight line D, and a straight line E. In fig. 1, the corresponding reference numerals of the respective straight lines are represented by symbols in circles.
Points 1 to 5 corresponding to the end points of the straight line, respectively, are defined as follows. Here, the element content in the case where the content of Ni is a mass% and the total content of Al and the like is b mass%, that is, the point where [ Ni ] ═ a and [ M ] ═ b is represented by (a, b). In fig. 1, corresponding reference numerals for the various points are indicated by numbers in blocks.
Point 1(0.1,0.01)
Point 2(11.0,0.01)
Point 3(11.0,7.00)
Point 4(3.0,10.00)
Point 5(0.1,7.00)
Each line is represented as a line connecting two points.
A straight line A: point 1 and point 2([ M ] ═ 0.01)
A straight line B: point 2 and point 3([ Ni ] ═ 11.0)
A straight line C: point 3 and point 4
A straight line D: point 4 and point 5
Line E: point 5 and point 1([ Ni ] ═ 0.1)
Here, the reason why the respective straight lines a to E are defined will be described.
Line a and line E ([ M ] ═ 0.01, [ Ni ] ═ 0.1):
in order to obtain a high saturation magnetic flux density while maintaining a low coercive force, the conditions of [ M ] 0.01 or more and [ Ni ] 0.1 or more are defined.
Specifically, in the case where [ Ni ] is 0.1 or more ([ Ni ]. gtoreq.0.1), B30000, which is a value of magnetic flux density measured under an external magnetic field H of 30,000A/m, is 1.7T or more (B30000. gtoreq.1.7T), can be reached. Here, B30000 is a value that can approximate the saturation magnetic flux density of such a soft magnetic alloy. Even if the magnetic flux density is not saturated in H of 30,000A/m, the saturation magnetic flux density will be larger than B30000. Therefore, B30000 can be considered as a lower limit value of the saturation magnetic flux density. In the soft magnetic alloy according to the embodiment of the present invention, the saturation magnetic flux density (B30000) is preferably 1.7T or more, more preferably 2.0T or more.
However, in an iron-based alloy containing only Ni as an additive element, if [ Ni ] is 0.1 or more, the crystal structure has α phase + γ phase or martensite phase, and thus the coercive force Hc exceeds 1,000A/M and becomes larger.accordingly, by adding an element selected from the group consisting of Al, Si and V and setting [ M ] to 0.01 or more ([ M ]. gtoreq.0.01), the formation of α phase is promoted, and it can be ensured that a low coercive force satisfying Hc.ltoreq.1,000A/m. α phase (ferrite phase) shows soft magnetism and γ phase (austenite phase) shows non-magnetism.
Line B ([ Ni ] ═ 11.0):
as described above, the saturation magnetic flux density can be increased by setting the Ni content to 0.1% or more. However, if too much Ni is contained, conversely, the saturation magnetic flux density decreases. The requirement that [ Ni ] is less than or equal to 11.0 can ensure that B30000 is more than or equal to 1.7T. A low coercive force of Hc.ltoreq.1,000A/m can be secured.
Line C and line D:
by controlling the Ni content, and the total content of Al and the like to values within the region defined by the straight line C and the straight line D, it is possible to ensure that B30000. gtoreq.1.7T.
As described above, the soft magnetic alloy according to the embodiment of the present invention has a high saturation magnetic flux density and a low coercive force, and exerts excellent soft magnetic characteristics. In addition, the soft magnetic alloy has high hardness. For example, the vickers hardness Hv may be set to 150 or more, 250 or more, and 350 or more. It is estimated that such high hardness is exerted by a soft magnetic alloy containing Ni, Al, and the like.
(composition of ingredients within the second region)
In the soft magnetic alloy according to the embodiment of the present invention, it is preferable that [ Ni ] and [ M ] exist within the second region within the first region.
As shown in fig. 1, the second region is defined as a hexagonal region surrounded by a straight line F and a straight line G described below in addition to the straight line a, the straight line C, the straight line D, and the straight line E.
The straight line F is defined as a straight line connecting the point 6 and the point 7.
Point 6(1.0,0.01)
Point 7(6.5,3.50)
The straight line G is defined as a straight line corresponding to [ Ni ] ═ 6.5. Here, the element content at the point p corresponding to the intersection of the straight line G and the straight line C is about the point p (6.5, 8.7).
Here, the reason why the straight lines F and G are defined will be described.
A straight line F:
the α phase in the crystal structure is easily maintained by controlling the content of Ni, and the total content of Al and the like to values within the region defined by the straight line F. therefore, the coercive force Hc can be suppressed to a low level.particularly, the coercive force Hc is easily reduced to a low level of Hc ≦ 500A/m. for example, even when heat treatment is performed at 850 ℃ which is a normal temperature during magnetic annealing of an electromagnetic steel sheet, the α phase can be highly maintained. α phase + γ phase or martensite phase is easily formed and the coercive force Hc is increased in the case where the content of Ni and/or Al and the like is a value outside the region defined by the straight line F. therefore, particularly, when the magnetic annealing is performed at a high temperature, the desired soft magnetic properties are hardly exhibited.
Straight line G ([ Ni ] ═ 6.5):
when [ Ni ] is 6.5 or less, a high saturation magnetic flux density of B30000. gtoreq.1.7T is easily ensured. In the case of [ Ni ] >6.5, Hc.ltoreq.500A/m can be guaranteed, but in some cases it may be difficult to achieve Hc.ltoreq.500A/m and B30000. gtoreq.1.7T simultaneously.
Further, the magnetic permeability can be improved by setting the content of Ni, and the total content of Al and the like within the second region. For example, a specific magnetic permeability μmay satisfy μ > 1000.
(composition of ingredients in the third region)
In the soft magnetic alloy according to the embodiment of the present invention, it is preferable that [ Ni ] and [ M ] exist within the third region within the second region.
As shown in fig. 1, the third region is defined as a pentagonal region surrounded by a straight line H and a straight line I described below in addition to the straight line D, the straight line E, and the straight line G.
The straight line H is defined as a straight line connecting the point 8 and the point 7.
Point 8(0.1,0.50)
Point 7(6.5,3.50)
The straight line I is defined as a straight line connecting the point 9 and the point 4.
Point 9(6.5,7.00)
Point 4(3.0,10.00)
In the case where the content of Ni, and the total content of Al and the like are present within the third region, in particular, the soft magnetic alloy is excellent in the effect of lowering the coercive force Hc to a low level due to the maintenance of the α phase, and it is easy to satisfy Hc ≦ 500A/m.
(addition of Cr or a combination of Cr and Mo)
The soft magnetic alloy according to the embodiment of the present invention may contain only Ni, which is an essential additional element in an amount within the first region (or the second region or the third region), and at least one element selected from the group consisting of Al, Si, and V, in addition to Fe and inevitable impurities. However, the soft magnetic alloy according to an embodiment of the present invention may further include at least one of Cr and Mo as an optional element. If the soft magnetic alloy contains at least one of Cr and Mo, the resistance and corrosion resistance of the soft magnetic alloy can be improved. The soft magnetic alloy may include either one of Cr and Mo, or may include both Cr and Mo. In view of effectively improving the corrosion resistance, it is preferable that the soft magnetic alloy contains at least Cr.
In the case where Cr is contained, the content of Cr is set to 1% or more and 14% or less. When the Cr content is 1% or more, the resistivity rho can be made high at a value of rho.gtoreq.70 mu omega cm. By increasing the resistance, eddy current losses in the soft magnetic alloy can be reduced. In addition, Cr has an effect of lowering the coercive force Hc. Under the condition that the content of Cr is more than 1 percent, Hc is easy to be less than or equal to 500A/m.
However, if the content of Cr is increased too much, the saturation magnetic flux density is liable to be lowered. By setting the Cr content to 14% or less, a high saturation magnetic flux density such as B30000. gtoreq.1.7T can be ensured. When Cr is less than or equal to 9%, the magnetic flux density can be maintained at a high saturation level. On the other hand, when Cr is greater than 9%, Cr is not less than 10%, and Cr is not less than 12%, particularly high effects of improving resistivity and corrosion resistance can be obtained.
In the case where Mo is contained, the content of Mo is preferably set to 1% or more and 6% or less. When the Mo content is 1% or more, an excellent effect of improving the resistivity and the corrosion resistance can be obtained. When the Mo content is 6% or less, a high saturation magnetic flux density can be ensured.
As described above, it is preferable that the soft magnetic alloy contains at least Cr, and in the case of adding Mo, it is preferable that the contents of Cr and Mo satisfy 1% or more and 14% or less and 1% or more and 6% or less, respectively. Such an embodiment containing both Cr and Mo may be regarded as an embodiment in which a combination of Cr and Mo obtained by replacing a part of Cr with Mo is added to the soft magnetic alloy. Mo has an excellent effect of improving resistance and corrosion resistance compared to Cr. Therefore, Mo can provide a high effect even with a small addition amount. In view of this, in the case of using a combination of Cr and Mo, it is more preferable to add Cr and Mo so that the sum of the contents of Cr and Mo, which is 3.3 times the content of Mo, is equal to the amount of Cr in the case of using only Cr. That is, from the viewpoint of improving the resistance and corrosion resistance while securing a high saturation magnetic flux density, the content may be set to satisfy 1% or more and 3.3Mo or less and 14% or less. Further, from the viewpoint of maintaining the high saturation magnetic flux density to a high level, the content may be set so as to satisfy Cr +3.3 Mo.ltoreq.9%. On the other hand, from the viewpoint of obtaining particularly high resistivity and corrosion resistance, the content may be set to satisfy Cr +3.3Mo > 9%, particularly Cr +3.3 Mo.gtoreq.10%, and more preferably Cr +3.3 Mo.gtoreq.12%. The reduction of the Cr content by the combined use of Mo contributes to maintaining a high magnetic flux density.
(other additional elements)
The soft magnetic alloy according to the embodiment of the present invention may further include, as a second optional element, at least one element selected from the following group, in addition to the essential element Ni, and at least one element selected from the group consisting of Al, Si, and V, or in addition to these essential elements, and at least one optional element of Cr and Mo:
0.03％≤Pb≤0.30％，
0.002％≤Bi≤0.020％，
0.002％≤Ca≤0.20％，
te is 0.01% or more and 0.20% or less, and
0.03％≤Se≤0.30％。
the machinability of the soft magnetic alloy can be improved by adding at least one element selected from the group of second optional elements. The lower limit of each second optional element is defined as a content capable of providing an effect of improving machinability. On the other hand, the upper limit of each second optional element is defined as a content capable of avoiding a decrease in magnetic properties.
Examples
The present invention will be more specifically described by using examples.
As examples a1 to a12 and B1 to B18 and comparative examples 1 to 9, respective soft magnetic alloys having the composition (unit: mass%) shown in tables 1 and 2 were prepared. Furthermore, with respect to some soft magnetic alloys of group B-examples shown in table 2, the corresponding soft magnetic alloys of group B' -examples were prepared by adding the additive elements shown in table 3. The balance of the composition of each component is Fe and inevitable impurities. Specifically, metallic materials having respective composition ratios are melted in a vacuum induction melting furnace, and cast and hot forged. Machining was performed so as to have the shape of a measurement test piece for the test described below, and then magnetic annealing was performed at 850 ℃.
The measurement test piece obtained in this manner was subjected to measurement of each of the magnetic flux density B30000, coercive force Hc, resistivity ρ, and hardness, and evaluation of corrosion resistance. Further, for some of the test pieces for measurement, machinability evaluation was also performed. The method for each test will be described below.
< measurement of magnetic flux Density >
A soft magnetic alloy is machined into a cylindrical shape having an outer diameter of 28mm, an inner diameter of 20mm, and a thickness t of 3mm, thereby preparing a magnetic ring (iron core): a primary coil (480 turns) and a secondary coil (20 turns) are formed by using the magnetic ring, and the formed coils are used as a measurement sample the magnetic flux density is measured by using a magnetic measuring instrument ("BH-1000", manufactured by Denshijiki industringco., <tt translation = L ">l &ttt/t >tt td.): the magnetic flux density is measured in such a manner that a current flows in the primary coil to generate a magnetic field H around the magnetic ring, and the magnetic flux density generated in the magnetic ring is calculated based on an integrated value of a voltage induced in the secondary coil in which the magnetic field H is set to 30,000A/m and B30000 as a value of the magnetic flux density is recorded at this time.
< measurement of coercive force >
The magnetization curve (B-H curve) was measured by using the same measurement sample and the same magnetic measurement device as those used for the measurement of the magnetic flux density. The coercivity Hc was evaluated based on the obtained hysteresis loop.
< measurement of resistivity >
Machining of soft magnetic alloys to a cross section of 10mm2A prism shape having a length of 30 mm. Then, the resistivity was measured. The measurement was performed by using a four-terminal method.
< evaluation of Corrosion resistance >
The corrosion resistance of the soft magnetic alloy was evaluated by the salt spray test specified in JIS Z2371. That is, salt water spraying was performed, and after 24 hours, the surface of the sample was visually observed. The ratio of the area of the region where generation of rust was confirmed was estimated as the rust occurrence rate. Since the value of the occurrence rate of rust becomes small, high corrosion resistance is achieved.
< measurement of hardness >
Machining of soft magnetic alloys to have a thickness of 1cm3Embedded in a resin and then polished. The vickers hardness (Hv) of the sample piece was measured by using a vickers hardness tester.
< evaluation of machinability >
Some of the soft magnetic alloys of group B examples and group B' -examples were subjected to machinability tests and evaluated for machinability. That is, a flat plate-shaped sample having a thickness of 5mm was prepared, and through-holes (holes) were formed thereon by using a drill having a diameter of 2mm until the drill was worn and became unable to form through-holes any more. The total number of through holes formed was counted to evaluate the machinability of the sample. The processing speed was set at 20 m/min. The case where 81 or more through holes can be formed was evaluated as "excellent", the case where 51 or more and 80 or less through holes can be formed was evaluated as "good", and the case where only 50 or less through holes can be formed was evaluated as "poor".
< results >
Table 1 shows the composition of the soft magnetic alloys in examples a1 to a12 and comparative examples 1 to 9 and the results of the above tests. With respect to examples a1 to a10, the content of Ni, and the total content of Al and the like correspond to point 1 to point 10 indicated by numerals in the boxes of fig. 1, respectively. With regard to comparative examples 2 to 9, the content of Ni, and the total content of Al and the like correspond to the points indicated by the numerals in parentheses. Comparative example 1 corresponds to pure iron.
According to table 1, in each example in which the content of Ni, and the total content of Al and the like are present within the first region, the magnetic flux density B30000 is 1.7T or more, and the coercive force Hc is 1,000A/m or less. That is, this shows that in the case where Ni, and at least one element selected from the group consisting of Al, Si, and V are added to Fe at a content within the first region, an excellent soft magnetic alloy having a low coercive force and a high saturation magnetic flux density can be obtained. Further, in comparing the example a10 and the examples a11 and a12 which are different from each other only in whether or not Cr and Mo are added, it can be found that, as in the examples a11 and a12, with the addition of Cr or a combination of Cr and Mo, high resistance and high corrosion resistance are achieved while maintaining high magnetic flux density and low coercive force.
In contrast, in comparative example 1 using pure iron, a high magnetic flux density and a low coercive force were achieved, but the corrosion resistance was poor and the resistivity ρ was also low. In comparative example 2 in which Al, Si, and V were not contained and a large amount of Ni was contained, the magnetic flux density B30000 was a high value, but the coercive force Hc exceeded 1,000A/m and the soft magnetic characteristics were poor. In comparative example 3, the coercive force Hc was also high because Al was contained but the content thereof was too low. Even in comparative examples 4, 8 and 9, the coercive force Hc was high because the content of Ni was excessive. Comparative examples 4, 8 and 9 contained Al, Si and V, respectively, as additional elements other than Ni. Comparative examples 4, 8 and 9 are similar to each other in the content of Ni and each additional element, and therefore, they all show a large coercive force Hc exceeding 2,000A/m. In comparative examples 5 and 6, the Ni content and the Al content were located in the regions outside the straight lines C and D that define the first region. Therefore, the magnetic flux density B30000 is less than 1.7T. In comparative example 7, since Ni was not contained, the magnetic flux density B30000 was less than 1.7T.
Table 2 shows the composition of the soft magnetic alloys in examples B1 to B18 including the case where the content of Cr and/or Mo was increased and the results of the above tests.
From table 2, it is understood that particularly high resistivity and corrosion resistance are achieved with a content of Cr (or Cr +3.3Mo) of more than 9%, as in examples B1 to B17. In particular, when comparing example B1 and example B3 in which the contents of Ni and Al or V are the same but the contents of Cr are different from each other, it can be found that in example B3 having a higher Cr content, the resistivity and the corrosion resistance are improved. A decrease in coercivity is also observed. In addition, when comparing example B10 in which the contents of Ni, Al and Mo are almost the same with example B11, it can be found that the resistivity and the corrosion resistance are improved in example B10 having a higher Cr content.
When comparing example B1 and example B5, which differ only in the presence or absence of Mo addition, it was found that when Mo is added in addition to Cr, the resistivity and corrosion resistance are improved. In addition, when comparing example B17 in which the contents of Ni and Al are the same but Cr is not included with example B18, it can be found that the resistivity and the corrosion resistance are improved in example B17 having a higher Mo content. Further, although examples B12 and B13 were the same in the content of Ni and almost the same as each other in the content of Al, the resistivity was higher in example B13 having a larger Cr +3.3Mo value. Further, examples B15 to B18 were identical to each other in terms of Ni and Al contents, but the values of Cr +3.3Mo were different. That is, the examples B15 to B17 had larger values of Cr +3.3Mo than the example B18. In comparing examples B15 to B18, it can be found that examples B15 to B17 achieve high corrosion resistance as compared to example B18.
Examples B10 to B18 show low hardness compared to examples B1 to B9. The present inventors considered that this is because the examples B10 to B18 had a large Al/Ni content ratio of, for example, 1 or more, and therefore, had a large contribution from the ferrite structure. However, in examples B10 to B18, by setting the content of Cr to be relatively low or by not including Cr, a high magnetic flux density can be maintained even with a small Ni content. Thus, by setting the value of Cr +3.3Mo large by adding Mo, high resistivity and high corrosion resistance can be maintained even with a small Cr content.
Further, as shown in table 2, soft magnetic alloys of examples B1 ', B2', B5 ', B6', B8 ', and B11' were prepared by adding at least one element selected from the group consisting of Pb, Bi, Ca, Te, and Se to the constituent compositions of examples B1, B2, B5, B6, B8, and B11, respectively. The relationship between machinability and the presence or absence of these added elements was evaluated. Table 3 shows the evaluation results of the component composition and machinability. In addition, although table 3 does not provide data, the present inventors have confirmed that all of the B' -set examples containing the additive elements show magnetic flux densities, coercive forces, resistivity, corrosion resistance, and hardness at similar levels to those obtained in the corresponding B-set examples as shown in table 2.
TABLE 3
According to table 3, even in the B-group examples containing no element selected from the group consisting of Pb, Bi, Ca, Te, and Se, relatively good machinability was achieved. However, it is understood that in the B' -group embodiment containing at least one element selected from the group consisting of Pb, Bi, Ca, Te, and Se, the machinability is significantly improved. Namely, it was confirmed that Pb, Bi, Ca, Te and Se have an effect of improving the machinability of the soft magnetic alloy.
While the invention has been described in detail and with reference to specific embodiments and examples, it will be apparent to one skilled in the art that various changes and modifications can be made therein without departing from the spirit and scope thereof.
The present application is based on japanese patent application No. 2016-.
Claims (12)
1. A soft magnetic alloy, comprising:
ni, and
at least one element selected from the group consisting of Al and V, and
the balance being Fe and unavoidable impurities,
the inevitable impurities include Cu not more than 0.1 mass%, C not more than 0.04 mass%, N not more than 0.06 mass%, or O not more than 1 mass%,
wherein when the content of Ni, and the total content of Al and V are represented by [ Ni ] and [ M ] in mass%, respectively, and the relationship between [ Ni ] and [ M ] is plotted, the coordinates ([ Ni ], [ M ]) exist within a region surrounded by the following straight line A, the following straight line B, the following straight line C, the following straight line D, and the following straight line E:
a straight line A: [ M ] ═ 0.01;
a straight line B: [ Ni ] ═ 11.0;
a straight line C: a straight line connecting a point ([ Ni ], [ M ]) of (11.0,7.00) and a point ([ Ni ], [ M ]) of (3.0, 10.00);
a straight line D: a straight line connecting a point ([ Ni ], [ M ]) of (3.0,10.00) and a point ([ Ni ], [ M ]) of (0.1, 7.00); and
line E: [ Ni ] ═ 0.1,
wherein the soft magnetic alloy has a saturation magnetic flux density of 1.7T or more and a coercive force of 1,000A/m or less,
the soft magnetic alloy has a crystal structure of α phase and exhibits soft magnetism,
the soft magnetic alloy forms an iron core or a magnetic yoke.
2. The soft magnetic alloy of claim 1, further comprising, in mass%:
1％≤Cr≤14％。
3. the soft magnetic alloy of claim 1, further comprising, in mass%:
1％≤Mo≤6％。
4. the soft magnetic alloy of claim 2, further comprising, in mass%:
1％≤Mo≤6％。
5. the soft magnetic alloy according to claim 1, further comprising Cr and Mo, and satisfying 1% Cr +3.3Mo < 14% by mass.
6. The soft magnetic alloy according to claim 2, further comprising Cr and Mo, and satisfying 1% Cr +3.3Mo < 14% by mass.
7. The soft magnetic alloy according to claim 3, further comprising Cr and Mo, and satisfying 1% Cr +3.3Mo < 14% by mass.
8. The soft magnetic alloy according to claim 4, further comprising Cr and Mo, and satisfying 1% Cr +3.3Mo < 14% by mass.
9. Soft magnetic alloy according to any of claims 1 to 8,
wherein the coordinates ([ Ni ], [ M ]) are present within a region enclosed by the straight line A, the straight line C, the straight line D, the straight line E, the following straight line F, and the following straight line G:
a straight line F: a straight line connecting a point ([ Ni ], [ M ]) of (1.0,0.01) and a point ([ Ni ], [ M ]) of (6.5, 3.50); and
a straight line G: [ Ni ] ═ 6.5.
10. The soft magnetic alloy according to claim 9,
wherein the coordinates ([ Ni ], [ M ]) are present within a region enclosed by the straight line D, the straight line E, the straight line G, the following straight line H, and the following straight line I:
a straight line H: a straight line connecting a point ([ Ni ], [ M ]) of (0.1,0.50) and a point ([ Ni ], [ M ]) of (6.5, 3.50); and
a straight line I: and a straight line connecting a point ([ Ni ], [ M ]) of (6.5,7.00) and a point ([ Ni ], [ M ]) of (3.0, 10.00).
11. The soft magnetic alloy according to any one of claims 1 to 8, further comprising at least one element selected from the group consisting of:
0.03％≤Pb≤0.30％，
0.002％≤Bi≤0.020％，
0.002％≤Ca≤0.20％，
te is 0.01% or more and 0.20% or less, and
0.03％≤Se≤0.30％。
12. the soft magnetic alloy according to any one of claims 1 to 8, having a Vickers hardness Hv of 250 or more.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2016-136661 | 2016-07-11 | ||
| JP2016136661 | 2016-07-11 | ||
| JP2017116521A JP6859862B2 (en) | 2016-07-11 | 2017-06-14 | Soft magnetic alloy |
| JP2017-116521 | 2017-06-14 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN107610869A CN107610869A (en) | 2018-01-19 |
| CN107610869B true CN107610869B (en) | 2020-07-14 |
Family
ID=61019957
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201710562865.0A Active CN107610869B (en) | 2016-07-11 | 2017-07-11 | Soft magnetic alloy |
Country Status (2)
| Country | Link |
|---|---|
| JP (1) | JP6859862B2 (en) |
| CN (1) | CN107610869B (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP6911294B2 (en) * | 2016-07-12 | 2021-07-28 | Tdk株式会社 | Soft magnetic metal powder and powder magnetic core |
| JP7247874B2 (en) * | 2019-01-07 | 2023-03-29 | 新東工業株式会社 | Iron-based soft magnetic alloy powder |
| JP7355234B2 (en) * | 2020-10-29 | 2023-10-03 | Ｊｆｅスチール株式会社 | electromagnetic soft iron |
| JP2021061408A (en) * | 2020-12-04 | 2021-04-15 | Tdk株式会社 | Soft magnetic metal powder and powder-compact magnetic core |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101215679A (en) * | 2008-01-08 | 2008-07-09 | 厦门大学 | Nonmagnetic iron-base block amorphous alloy and preparation method thereof |
| JP2015201481A (en) * | 2014-04-04 | 2015-11-12 | Ｎｅｃトーキン株式会社 | Powder-compact magnetic core arranged by use of nanocrystal soft magnetic alloy powder, and manufacturing method thereof |
Family Cites Families (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01184250A (en) * | 1988-01-14 | 1989-07-21 | Alps Electric Co Ltd | Fe-ni-si-al magnetic material |
| JP2000160302A (en) * | 1998-11-19 | 2000-06-13 | Sanyo Special Steel Co Ltd | Electromagnetic stainless steel excellent in cold forgeability |
| JP4115610B2 (en) * | 1998-12-03 | 2008-07-09 | 山陽特殊製鋼株式会社 | Electromagnetic stainless steel with excellent low temperature toughness |
| JP2000345292A (en) * | 1999-06-04 | 2000-12-12 | Daido Steel Co Ltd | Manufacture of nitrocarburizing steel and nitrocarburized parts |
| CN101710521A (en) * | 2009-12-18 | 2010-05-19 | 浙江大学 | Iron-based nanocrystalline soft magnetic alloy with electromagnetic interference resistance and preparation method thereof |
| WO2012001943A1 (en) * | 2010-06-30 | 2012-01-05 | パナソニック株式会社 | Composite magnetic material and process for production thereof |
| US20120189460A1 (en) * | 2011-01-21 | 2012-07-26 | General Electric Company | Welded Rotor, a Steam Turbine having a Welded Rotor and a Method for Producing a Welded Rotor |
| CN103774047B (en) * | 2012-10-20 | 2017-03-01 | 大同特殊钢株式会社 | There is the mould steel of excellent thermal conductance, mirror polishability and toughness |
| CN102982956B (en) * | 2012-11-08 | 2015-03-18 | 建德市易通金属粉材有限公司 | High magnetic permeability and low loss metal soft magnetic material powder and preparation method thereof |
-
2017
- 2017-06-14 JP JP2017116521A patent/JP6859862B2/en active Active
- 2017-07-11 CN CN201710562865.0A patent/CN107610869B/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101215679A (en) * | 2008-01-08 | 2008-07-09 | 厦门大学 | Nonmagnetic iron-base block amorphous alloy and preparation method thereof |
| JP2015201481A (en) * | 2014-04-04 | 2015-11-12 | Ｎｅｃトーキン株式会社 | Powder-compact magnetic core arranged by use of nanocrystal soft magnetic alloy powder, and manufacturing method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JP6859862B2 (en) | 2021-04-14 |
| CN107610869A (en) | 2018-01-19 |
| JP2018012883A (en) | 2018-01-25 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN107610869B (en) | Soft magnetic alloy | |
| JP6929005B2 (en) | Ultra-low cobalt iron-cobalt magnetic alloy | |
| JP4399751B2 (en) | Composite magnetic member, method for manufacturing ferromagnetic portion of composite magnetic member, and method for forming nonmagnetic portion of composite magnetic member | |
| JP2014198874A (en) | Steel material excellent in corrosion resistance and magnetic properties and method of producing the same | |
| JPH0542493B2 (en) | ||
| JP2013049918A (en) | Electromagnetic stainless steel and method of manufacturing the same | |
| US11482355B2 (en) | Soft magnetic alloy | |
| JP6222498B2 (en) | Metastable austenitic stainless steel strip or steel plate | |
| JP4094583B2 (en) | Composite material having non-magnetic part and method for producing the same | |
| JP2022056669A (en) | Ferritic stainless steel | |
| JP2003226945A (en) | Soft magnetic steel having excellent cold forgeability and magnetic permeability, soft magnetic steel parts having excellent magnetic permeability and production method therefor | |
| JP2004307977A (en) | Wire rod of nonmagnetic sulfur free-cutting stainless steel superior in cold drawability and corrosion resistance | |
| JPWO2012077631A1 (en) | Composite magnetic material and composite magnetic material | |
| JPH11279717A (en) | Free cutting corrosion resistant soft magnetic material | |
| JP7355234B2 (en) | electromagnetic soft iron | |
| CN114981465B (en) | Non-magnetic austenitic stainless steel | |
| JP2023065295A (en) | Semi-hard magnetic steel and semi-hard magnetic steel component | |
| WO2023074160A1 (en) | Semi-hard magnetic steel component | |
| JPH08120420A (en) | Corrosion resistant soft-magnetic steel | |
| WO2023084756A1 (en) | Soft magnetic iron | |
| JP2001073101A (en) | Electromagnetic material having high magnetic flux density and high specific resistance and excellent in machinability and cold forgeability | |
| JP4211228B2 (en) | Fe-Co soft magnetic material | |
| JP3561922B2 (en) | Manufacturing method of soft magnetic stainless steel | |
| CN118159676A (en) | Semi-hard magnetic steel part | |
| JPS61213353A (en) | Non-magnetic stainless steel excelling in spring characteristic |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |