JP2967415B1 - Stirring continuous casting of Al alloy - Google Patents

Abstract

Abstract: PROBLEM TO BE SOLVED: To suppress agglomeration of Fe-based intermetallic compounds in an ingot peripheral region and to avoid segregation of various intermetallic compounds in an ingot central region. SOLUTION: In the stirring continuous casting method of Al alloy,
The molten metal m of the Al alloy composition is introduced into the cylindrical mold 13 disposed immediately below the spout 15 while being electromagnetically stirred in the spout 15. As the molten metal m of the Al alloy composition, the Fe content is [3/4] wt% ≦ Fe <[5/3] wt%,
When the Mn content is [Fe / 5] wt% ≦ Mn <[− Fe
+2] wt%. The magnetic flux density B ₁ in the molten metal stirring area forming portion b on the inner peripheral surface a of the spout is set to 100
Gs ≦ B ₁ <500 Gs, and the magnetic flux density B ₂ in the central region c of the molten metal stirring region A is set to B ₂ ≦ 20 Gs.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a continuous stirring method for an Al alloy, and more particularly, to a continuous casting method in which a molten metal having an Al alloy composition is electromagnetically stirred in a spout and is introduced into a cylindrical mold disposed immediately below the spout. About the law.

[0002]

2. Description of the Related Art Conventionally, an Al alloy ingot obtained by a stirring continuous casting method has been used, for example, as a casting material for thixocasting. In the thixocasting method, molding is performed using the fluidity of a semi-solid casting material in which a solid phase and a liquid phase coexist. It is.

However, when a recycled material is used as a raw material due to a demand for resource saving, C in the recycled material is
When the content of u, Mn, Ti, etc. is increased, the high-melting acicular intermetallic compound crystallizes coarsely, and the coarse acicular intermetallic compound cannot be refined only by the electromagnetic stirring force. occured.

Therefore, the present inventors have proposed to use a molten alloy having an Al alloy composition having an Fe content of Fe ≧ [3/4] wt% so that the crystallization temperature of primary crystal α is equal to or higher than that. At a high temperature, a hard Fe-based intermetallic compound is crystallized as a primary crystallized substance, and the Fe-based intermetallic compound is moved around in a liquid phase at random by an electromagnetic stirring force, and a primary crystal α and a coarse needle are formed. A continuous agitation casting method has been developed in which the intermetallic compound is crushed and refined.
No. 103893 and drawings).

[0005]

The inventors of the present invention have further studied the agitated continuous casting method, and as a result, depending on the Mn content in the molten metal, the Fe-based intermetallic compound agglomerates in the outer peripheral region of the ingot. It has been clarified that, since relatively large aggregates are formed, the crushing and refining effect of the Fe-based intermetallic compound may not be sufficiently obtained.

Further, since the aggregate is chemically stable, it is difficult to reduce the size of the aggregate by an additional element. In addition, since the aggregate has a high melting point, it is difficult to reduce the size of the aggregate by heat treatment. When thixocasting is performed using a casting material containing such an agglomerate, the agglomerate is collected in the Al alloy member as it is, so that the toughness and elongation of the member are significantly reduced.

[0007]

SUMMARY OF THE INVENTION It is an object of the present invention to greatly suppress the agglomeration of Fe-based intermetallic compounds in the peripheral region of an ingot made of an Al alloy and to avoid segregation of various intermetallic compounds in the central region of the ingot. It is an object of the present invention to provide an agitated continuous casting method capable of performing the above-described method.

[0008] To achieve the above object, according to the present invention,
In a stirring continuous casting method in which a molten metal having an Al alloy composition is electromagnetically stirred in a spout and introduced into a cylindrical mold disposed directly below the spout, the molten metal having the Al alloy composition is
e content is [3/4] wt% ≦ Fe <[5/3] wt%
And the Mn content is [Fe / 5] wt% ≦ Mn <
[−Fe + 2] wt%, and the magnetic flux density B ₁ in the molten metal stirring area forming portion on the inner surface of the spout is 100 Gs ≦ B ₁ <500 Gs, and the magnetic flux density B ₂ in the central area of the molten metal stirring area. Is set to B ₂ ≦ 20 Gs, respectively.

When the Fe content is specified as above in the molten alloy having the Al alloy composition, hard Fe as a primary crystallized material is formed at a high temperature equal to or higher than the crystallization temperature of the primary crystal α.
The intermetallic compound is crystallized in the vicinity of the melt stirring area forming portion on the inner peripheral surface of the spout. In this case, if the Mn content is within the above range, the Fe-based intermetallic compound is likely to aggregate.

Therefore, the magnetic flux density B ₁ in the molten metal stirring region forming portion is set as described above, and the electromagnetic stirring force for the molten metal in the vicinity of the forming portion is increased, so that the Fe-based intermetallic compound is positively dispersed. And its aggregation is greatly suppressed. This makes it possible to sufficiently obtain the crushing and miniaturizing effect of the Fe-based intermetallic compound. However, when the magnetic flux density B ₁ is B ₁ <100 Gs, F
Aggregation of the e-based intermetallic compound is likely to occur, while B ₁
At ≧ 500 Gs, the electromagnetic stirring force is too strong, so that the unsolidified portion inside the ingot breaks through the solidified portion on the outer periphery,
That is, there is a possibility that a breakout occurs and casting becomes impossible.

On the other hand, the magnetic flux in the central region of the molten metal stirring region
Density B_TwoIs set as above, the final ingot
The flow of the molten metal in the central zone, which is the solidification zone, is minimized
Segregation of the seed intermetallic compound and the like can be avoided. did
Therefore, the magnetic flux density B_TwoHas B _Two= 0 Gs is also included. Was
However, the magnetic flux density B_TwoIs B_Two> 20Gs in ingot
The flow of the molten metal in the heart region becomes remarkable and intermetallic compounds etc.
Segregation occurs.

[0012] In the molten Al alloy composition, when the Fe content is Fe <[3/4] wt%, the addition of Fe has no significance.
On the other hand, when Fe ≧ [5/3] wt%, the crystallization amount of the Fe-based intermetallic compound becomes excessive, so that the toughness of the Al alloy member by thixocasting is significantly reduced. When the Mn content is Mn <[Fe / 5] wt%, no aggregation of the Fe-based intermetallic compound occurs, and on the other hand, Mn ≧ [−Fe
At +2] wt%, the toughness of the Al alloy member due to thixocasting is significantly reduced.

[0013]

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS An agitated continuous casting apparatus 1 shown in FIGS. 1 and 2 has a body 2 whose axis is directed vertically. The body 2 includes an inner peripheral wall 3, an outer peripheral wall 4 arranged at a predetermined interval on the outer peripheral side, an annular upper end wall 5 on the upper end side of the two walls 3, 4, And an annular lower end wall 6 located at the lower end side.

The inner peripheral wall 3 is composed of an upper cylindrical body 7 and a lower cylindrical body 8, and an inward annular portion 10 of an annular rubber seal 9 fitted to a lower outer peripheral surface of the upper cylindrical body 7 is provided between the two cylindrical bodies 7, 8. It is sandwiched and seals between them. In the upper cylinder 7, the lower half thereof is formed to be thicker than the upper half 12 so that the annular step 11 is formed inside, and constitutes a cylindrical water-cooled mold 13 as a cylindrical mold. I do. The water-cooled mold 13 is made of an Al alloy (for example, A5052).

A spout 15 is fitted into the upper half portion 12 via a thin cylinder 14 so as to be positioned coaxially with the water-cooled mold 13, and has an annular lower end face 17 forming a downward molten metal outlet 16. Abuts on the annular step portion 11. Also spout 1
An annular retaining plate 18 is fitted to a portion of the projection 5 protruding from the upper end wall 5, and the retaining plate 18 is fixed to the upper end wall 5.
The spout 15 is made of calcium silicate having adiabatic fire resistance. Alumina as spout constituent material,
Silica or the like is also used. Above the spout 15, a molten metal supply gutter 19 for horizontally pouring the molten metal m of the Al alloy composition is arranged, and a downwardly directed hot water supply port 20 communicates with an upwardly directed molten metal receiving port 21 of the spout 15.

In the body 2, the outer peripheral wall 3,
An electromagnetic induction type stirrer 23 is provided in the cylindrical closed space 22 between the four, and the stirrer 23 applies an electromagnetic stirring force to the molten metal m in the spout 15. As also shown in FIG.
Has a laminated iron core 24 having a tubular shape, and twelve coils 25 wound around the laminated iron core 24. The layered iron core 24 includes a cylindrical portion 26 and twelve ridges 27 that are arranged on the inner peripheral surface of the cylindrical portion at equal circumferential intervals and extend in the generatrix direction. Each coil 25 is wound around the adjacent two ridges 27 so that one ridge 27 overlaps a part of the two coils 25. Therefore, the electromagnetic induction type stirrer 23 has a four-pole coil. In this case, the stirrer 23 may be provided with a multi-pole coil exceeding a 4-pole coil.

A thin-walled coil stopping cylinder 28 is fitted inside the stratified iron core 24 so that the tips of the ridges 27 are in close contact with each other. 9 and is fixed in the cylindrical closed space 22. The stratified iron core 24 is mounted on an annular support member 29 of the lower end wall 6 and a plurality of bolts 30 and nuts 3
Fixed by 1. A plurality of connecting tools 32 are prepared in two ratios for one coil 25, and each connecting tool 32 is attached to the lower end wall 6 by watertight means through the lower end wall 6.

A plurality of water supply ports 33 are formed in the outer peripheral wall 4,
Cooling water w is supplied into the closed space 22 through each water supply port 33. A plurality of through holes 34 are formed in the cylindrical body 28 inside the laminated iron core 24 near the upper end thereof, so that a cooling water reservoir 35 exists above the annular rubber seal 9. The water-cooled mold 13 is cooled by the cooling water sump 35 and has a plurality of jet holes 36 for jetting the cooling water w of the cooling water sump 35 obliquely downward. The through hole 34 is also formed on the lower side of the cylindrical body 28.

In order to supply lubricating oil between the water-cooled mold 13 and the molten metal m, there are the following lubricating oil passages around the spout 15. In the inner peripheral wall 3, a lower plate 37 of the upper end wall 5 is integrally provided at an upper end of the upper cylindrical body 7.
An annular path 39 surrounding the spout 15 and a plurality of straight paths 40 extending radially from the annular path 39 are provided between the upper plate 38 and the lower plate 37 of the upper end wall 5. An inlet 41 formed in the upper plate 38 communicates with an end of each straight path 40, and the inlet 41 is connected to a refueling pump. As clearly shown in FIG. 2, a cylindrical path 42 is formed between the inner peripheral surface of the upper half 12 of the upper cylindrical body 7 and the outer peripheral surface of the cylindrical body 14.
In addition, a plurality of obliquely downward facing through holes 43 communicating between the annular passages 39 are formed in a continuous portion between the upper half portion 12 and the lower plate 37. The lower end of the cylindrical path 42 communicates with a plurality of V-shaped outlets 44 radially arranged between the annular step 11 and the annular lower end face 17 of the spout 15.

The molten metal stirring area A in the spout 15
Is a space surrounded by a group of coils 25 having a substantially cylindrical shape, that is, an intermediate portion in the spout 15 located at the same height position as the upper end surface of the group of coils 25, and a melt outlet 16.
The molten metal stirring area forming portion b on the spout inner peripheral surface a forms a curved surface. Furthermore, the inner radius of the molten metal outlet 16 of the spout 15 and r _1, whereas, the inner radius of the water-cooled mold 13 when the r _2, between the two within a radius r _1, r _2, r ₁
<R ₂ and r ₂ −r ₁ = Δr (where Δr is the overhang amount of the spout 15). That is, spout 1
5 has an annular overhang 15a around the melt outlet 16 thereof.

As the molten metal m of the Al alloy composition, the Fe content is [3/4] wt% ≦ Fe <[5/3] wt%, and the Mn content is [Fe / 5] wt% ≦ Mn <[-
Fe + 2] wt% is used. That is, FIG.
, When the Fe content is taken on the x-axis and the Mn content is taken on the y-axis, respectively, the line Fe = Ｆｅ, the line Mn = Fe
A triangular region surrounded by / 5 and the line Mn = -Fe + 2 is the composition range of the Al alloy. However, the line Mn = -Fe
The composition above +2 is not included in the above composition range.

In FIG. 1, a molten metal m having the above Al alloy composition
Is supplied from the hot water supply port 20 of the molten metal supply gutter 19 into the spout 15, the molten metal m is introduced into the water-cooled mold 13 disposed immediately below the spout 15 while being electromagnetically stirred by the agitator 23 in the spout 15, and cooled therein. Thus, an ingot I is obtained. In this casting process, the magnetic flux density B at the molten metal stirring area forming portion b on the spout inner peripheral surface a
₁ is 100 Gs ≦ B ₁ <500 Gs, and the magnetic flux density B ₂ in the central region c of the molten metal stirring region A is B ₂ ≦ 20 Gs
(Including B ₂ = 0 Gs).

When the Fe content in the molten alloy m of the Al alloy composition is specified as described above, at a high temperature equal to or higher than the crystallization temperature of the primary crystal α, hard F
The e-based intermetallic compound is crystallized in the vicinity of the molten metal stirring area forming portion b on the inner peripheral surface a of the spout. In this case, when the Mn content is in the above range, the Fe-based intermetallic compound is likely to aggregate.

Therefore, the magnetic flux density B ₁ in the molten metal stirring region forming portion b is set as described above, and the forming portion b
Since the electromagnetic stirring force with respect to the nearby molten metal m is increased, the Fe-based intermetallic compound is positively dispersed, and its aggregation is greatly suppressed. This makes it possible to sufficiently obtain the crushing and miniaturizing effect of the Fe-based intermetallic compound.

On the other hand, when the magnetic flux density B ₂ in the central area c of the molten metal stirring area A is set as described above, the ingot I
The flow of the molten metal m in the central region d, which is the final solidification region, can be suppressed as much as possible to avoid segregation of various intermetallic compounds and the like.

The control of the magnetic flux densities B ₁ and B ₂ as described above can be easily achieved by the electromagnetic induction type stirrer 23 having the four-pole coil.

That is, FIG. 5 shows a magnetic flux distribution at a certain moment by a four-pole coil (the number of coils: 12) connected to a three-phase power supply (U, V, W). In the case of this magnetic flux distribution, each magnetic field line e
Exists in the outer peripheral area f of the molten metal stirring area A, but in the central area c
Is almost nonexistent. Therefore, while the magnetic flux density is high in the molten metal stirring area forming portion b on the inner peripheral surface a of the spout, the magnetic flux density is extremely low or zero in the central area c.

FIG. 6 shows a magnetic flux distribution at a certain moment by a two-pole coil (the number of coils: 6) connected to a three-phase power supply (U, V, W). In the case of this magnetic flux distribution, the line of magnetic force e always exists in the central region c of the molten metal stirring region A, and therefore the molten metal m flows due to the high magnetic flux density, and segregation of the intermetallic compound occurs.

The characteristic difference between the four-pole coil and the two-pole coil was confirmed by the following experiment. That is, as a short pillar made of Al alloy, the electric resistance ρ is 1.38 × 10 ⁻⁷ Ω ·
m and a diameter of 152 mm are prepared, and an electromagnetic induction type stirrer having a 4-pole coil is installed on the outer peripheral side of the short columnar body.
Was applied, and the relationship between the position at a certain distance from the outer peripheral surface on the radius of the short column and the magnetic flux density at that position was determined. The same experiment was performed using an electromagnetic induction stirrer having a two-pole coil, and the relationship between the position and the magnetic flux density at that position was determined.

FIG. 7 shows the results of the experiment. As is clear from FIG. 7, when a four-pole coil is used, the magnetic flux density of the short pole body decreases proportionally to the position of about 69 mm from the outer peripheral surface, and the magnetic flux density decreases at the position of about 69 mm. It becomes zero, which is the same at the central position of 76 mm. Therefore, when a four-pole coil is used, a central region c where the magnetic flux density is zero appears. On the other hand, when a two-pole coil is used, the magnetic flux density hardly decreases even if the coil is separated from the outer peripheral surface, and therefore, it is apparent that a high magnetic flux density exists even in the central region c. Example 1 Table 1 shows the composition of an example (1) of an Al alloy.

[0031]

[Table 1]

This example (1) falls within a triangular area as shown by a point (1) in FIG.

An ingot I was cast by the stirring continuous casting apparatus 1 using the example (1) of the Al alloy. Casting conditions were as follows: melting temperature: 730 ° C .; melt temperature immediately above spout 15: 650 ° C .; casting withdrawal speed: 150 mm / min; overhang amount of spout 15 Δr: 2 mm; diameter of ingot I:
152.4 mm; magnetic flux density in molten metal stirring area forming part b: 360 Gs (4-pole coil, 50 Hz); average cooling rate of molten metal m in molten metal stirring area forming part b: 10 ° C. /
s;

For comparison, an ingot I was cast under the same conditions as described above, using an agitated continuous casting apparatus having the same structure as described above, except that a two-pole coil was used instead of the four-pole coil.

With respect to both ingots I, the relationship between a position at a certain distance from the outer peripheral surface on the radius and the Fe content at that position was obtained, and the results shown in FIG. 8 were obtained. From FIG. 8, it can be seen that the distribution of Fe over the ingot radius is more uniform when the quadrupole coil is used than when the bipolar coil is used. It is clear that segregation of the Fe-containing intermetallic compound occurs in the central region when a two-pole coil is used.

Next, using the example (1) of the Al alloy, in the stirring continuous casting apparatus 1 having a four-pole coil, each coil 25
The molten metal stirring area forming part b
Changing the magnetic flux density B _1, except that the cast examples of the ingot I (1) ~ (11) under the same conditions. For comparison, an ingot I example (12) was cast using a stirring continuous casting apparatus having a two-pole coil and performing the same casting operation as described above. Examples (1) to (1) of each ingot I
Regarding 2), the length L of the longest part of the aggregate (Fe-based intermetallic compound) in the outer peripheral area was measured, and the presence or absence of segregation in the central area was examined.

[0037]

[Table 2]

In the casting examples 1 and 2 in Table 2, the magnetic flux density B ₁ of the molten metal stirring area forming portion b was set to B ₁ = 50 in the casting operation by the stirring continuous casting apparatus 1 having the 4-pole coil.
In these cases, breakout occurred and casting was impossible.

FIGS. 9 and 10, FIGS. 11 and 12 and FIGS. 13 and 14 show the metal structure and the length L of the longest portion of the aggregate of Examples (1), (2) and (7) of Ingot I, respectively. .

Next, thixocasting was performed using a casting material consisting of the example (1) of the Al alloy and obtained from a plurality of ingots having aggregates of different sizes.
1 alloy member was obtained. The casting conditions were such that the temperature of the casting material was 565.
C., injection speed 2.0 m / s, mold temperature 250 ° C.

FIG. 15 shows the relationship between the length L of the longest portion of the aggregate in the Al alloy member and the Charpy impact value (with a notch). In the figure, points (1) to (11) correspond to the case where examples (1) to (11) of ingot I in Table 2 are used as a casting material.

FIG. 15 shows that the length L of the longest part of the aggregate is L
≧ 600μm, Charpy impact of Al alloy members
It can be seen that the value decreases. Therefore, the length L is L
To achieve <600 μm, as shown in Table 2,
Magnetic flux density B of stirring region forming part b ₁To B₁Set to ≧ 100Gs
Need to be determined. Also avoid breakout
B for₁<500 Gs.

By adjusting the overhang amount Δr of the spout 15, the magnetic flux density B of the molten metal stirring area forming portion b can be adjusted.
_One can vary. Example 2 Table 3 shows the compositions of Examples (2) to (12) of the Al alloy.

[0044]

[Table 3]

In these examples (2) to (12), examples (2) to (7) fall within a triangular area as shown by points (2) to (7) in FIG. ) To (12) show FIG.
As shown by points (8) to (12) in FIG.

Using the examples (2) to (12) of the respective Al alloys, the example (2)
a) to (12a) were cast. These examples (2a) to
(12a) corresponds to the examples (2) to (12) of the Al alloy, respectively. The casting conditions were as follows: melting temperature: 730 ° C .; molten metal temperature immediately above the spout 15: 650 ° C .;
0 mm / min; overhang amount of spout 15 Δr: 2 mm; diameter of ingot I: 152.4 mm; molten metal stirring area forming part b
Magnetic flux density at 300 Gs (4-pole coil, 50H
z): The average cooling rate of the molten metal m in the molten metal stirring area forming part b was set to 10 ° C./s.

Examples (2a) to (12a) of each ingot I
About the presence or absence of aggregates in the outer peripheral area,
When the aggregate was present, the length L of the longest part was measured.

For comparison, examples (2) to (1) of each Al alloy were used.
Example 2 (2b) to (1) of ingot I under the same conditions as above using the stirring continuous casting apparatus having a two-pole coil using 2).
2b) was cast. These examples (2b) to (12) b correspond to the examples (2) to (12) of the Al alloy, respectively.

Examples (2b) to (12b) of each ingot I
About the presence or absence of aggregates in the outer peripheral area,
When the aggregate was present, the length L of the longest part was measured.

Table 4 shows the microscope and the measurement results.

[0051]

[Table 4]

As is apparent from Table 4, aggregates appear in the examples (2a), (2b) to (7a), and (7b) of the ingot I.
(7) Therefore, an Al alloy having a composition falling within the triangular region in FIG. 4 is an object of the present invention. Also, from Table 4, 4
When a pole coil is used, the length L of the longest portion of the aggregate is L <6.
It can be seen that it can be suppressed to 00 μm.

FIGS. 16 and 17 and FIGS. 18 and 1
Reference numeral 9 indicates the length L of the metal structure and the longest portion of the aggregate in Examples (6a) and (6b) of Ingot I, respectively.

FIG. 20 shows A by thixocasting.
The relationship between the sum of the Fe content and the Mn content, Fe + Mn, and the Charpy impact value (with a notch) in the 1-alloy member is shown. In the figure, the Al alloy members indicated by points (2) to (7) correspond to the cases where the casting materials obtained from the ingot examples (2a) to (7a) in Table 4 are used.

FIG. 20 shows that Fe + Mn is equal to or greater than Fe + Mn ≧ 2.
It can be seen that the Charpy impact value of the Al alloy member decreases when the content becomes wt%. Therefore, the target of the present invention, Al
The composition of the alloy does not include the composition on the line Mn = -Fe + 2 in FIG.

[0056]

According to the present invention, by employing the above-mentioned means, the aggregation of Fe-based intermetallic compounds in the outer peripheral region is greatly suppressed and segregation of various intermetallic compounds in the central region is avoided. A with good casting quality
It is possible to provide an agitated continuous casting method of an Al alloy capable of obtaining an 1 alloy ingot.

[Brief description of the drawings]

FIG. 1 is a longitudinal sectional view of an agitated continuous casting apparatus.

FIG. 2 is an enlarged view of a main part of FIG.

FIG. 3 is a plan view showing a relationship between a laminated core and a coil.

FIG. 4 is a graph showing Fe contents and Mn contents of various Al alloys.

FIG. 5 is an explanatory diagram showing formation of a magnetic flux by a four-pole coil.

FIG. 6 is an explanatory diagram showing formation of a magnetic flux by a two-pole coil.

FIG. 7 is a graph showing the relationship between the distance from the outer peripheral surface of the short column and the magnetic flux density.

FIG. 8 is a graph showing the relationship between the distance from the outer peripheral surface of the ingot and the Fe content.

FIG. 9 is a micrograph showing a metal structure of an ingot example (1).

FIG. 10 is an explanatory diagram showing the length L of the longest part of the aggregate in the ingot example (1).

FIG. 11 is a micrograph showing a metal structure of an ingot example (2).

FIG. 12 is an explanatory diagram showing the length L of the longest portion of the aggregate in the ingot example (2).

FIG. 13 is a micrograph showing a metal structure of an ingot example (7).

FIG. 14 is an explanatory diagram showing the length L of the longest part of the aggregate in the ingot example (7).

FIG. 15 is a graph showing the relationship between the length L of the longest part of the aggregate in the Al alloy member and the Charpy impact value.

FIG. 16 is a micrograph showing a metal structure of an ingot example (6a).

FIG. 17 is an explanatory diagram showing the length L of the longest portion of the aggregate in the ingot example (6a).

FIG. 18 is a micrograph showing a metal structure of an ingot example (6b).

FIG. 19 is an explanatory diagram showing the length L of the longest portion of the aggregate in the ingot example (6b).

FIG. 20: Fe content and Mn in an Al alloy member
It is a graph which shows the relationship between the sum Fe + Mn of content and Charpy impact value.

[Explanation of symbols]

 DESCRIPTION OF SYMBOLS 1 Stirring continuous casting apparatus 13 Cylindrical water-cooled mold (cylindrical mold) 15 Spout 23 Electromagnetic stirrer A Melt stirring area a Spout inner peripheral surface b Melt stirring area forming part c Central area m Melt

Continued on the front page (72) Inventor Takashi Ide, 1-10-1, Shinsayama, Sayama City, Saitama Prefecture Inside Honda Engineering Co., Ltd. (72) Inventor Kiyonobu Mizogami 1-10-1, Shinsayama, Sayama City, Saitama Prefecture Honda Engineering (56) References JP-A-58-119439 (JP, A) JP-A-5-38559 (JP, A) (58) Fields investigated (Int. Cl. ⁶ , DB name) B22D 11/00 B22D 11/10

Claims (2)

(57) [Claims] 1. A stirring continuous casting method in which a molten metal (m) having an Al alloy composition is electromagnetically stirred in a spout (15) and is introduced into a cylindrical mold (13) disposed immediately below the spout (15). As the molten metal (m) of the Al alloy composition,
Fe content is [3/4] wt% ≦ Fe <[5/3] wt
%, And the Mn content is [Fe / 5] wt% ≦ Mn
<[− Fe + 2] wt%, and the magnetic flux density B ₁ in the molten metal stirring area forming portion (b) on the inner peripheral surface (a) of the spout is 100 Gs ≦ B ₁ <500 Gs, and the molten metal stirring area ( Magnetic flux density B in central area (c) of A)
_2. A stirring continuous casting method for an Al alloy, wherein ₂ is set to B ₂ ≦ 20 Gs. 2. The agitated continuous casting method of an Al alloy according to claim 1, wherein the electromagnetic induction type stirrer (23) for electromagnetically stirring the molten metal (m) includes a multi-pole coil having four or more pole coils.