Patent Grant
8303730
The present invention relates to a manufacturing method of a grain-oriented electrical steel sheet suitable for an iron core of a transformer and the like.
Conventionally, secondary recrystallization has been utilized for manufacturing a grain-oriented electrical steel sheet. When the secondary recrystallization is utilized, it is important to control a texture, an inhibitor (grain growth inhibitor) and a grain structure. AlN has been mainly used as an inhibitor of a high magnetic flux density grain-oriented electrical steel sheet, and various studies have been conducted on the control thereof.
However, it is not easy to cause the secondary recrystallization stable, and it is difficult to obtain sufficient magnetic property through the conventional method.
Patent Document 1: Japanese Examined Patent Application Publication No. 40-15644
Patent Document 2: Japanese Laid-open Patent Publication No. 58-023414
Patent Document 3: Japanese Laid-open Patent Publication No. 05-112827
Patent Document 4: Japanese Laid-open Patent Publication No. 59-056522
Patent Document 5: Japanese Laid-open Patent Publication No. 09-118964
Patent Document 6: Japanese Laid-open Patent Publication No. 02-182866
Patent Document 7: Japanese Laid-open Patent Publication No. 2000-199015
Patent Document 8: Japanese Laid-open Patent Publication No. 2001-152250
Patent Document 9: Japanese Laid-open Patent Publication No. 60-177131
Patent Document 10: Japanese Laid-open Patent Publication No. 07-305116
Patent Document 11: Japanese Laid-open Patent Publication No. 08-253815
Patent Document 12: Japanese Laid-open Patent Publication No. 08-279408
Patent Document 13: Japanese Laid-open Patent Publication No. 57-198214
Patent Document 14: Japanese Laid-open Patent Publication No. 60-218426
Patent Document 15: Japanese Laid-open Patent Publication No. 50-016610
Patent Document 16: Japanese Laid-open Patent Publication No. 07-252532
Patent Document 17: Japanese Laid-open Patent Publication No. 01-290716
Patent Document 18: Japanese Laid-open Patent Publication No. 2005-226111
Patent Document 19: Japanese Laid-open Patent Publication No. 2007-238984
Patent Document 20: International Publication pamphlet No. WO 06/132095
The present invention has an object to provide a manufacturing method of a grain-oriented electrical steel sheet capable of stably obtaining good magnetic properties.
A manufacturing method of a grain-oriented electrical steel sheet according to the present invention, includes: heating a slab containing: C: 0.04 mass % to 0.09 mass %; Si: 2.5 mass % to 4.0 mass %; acid-soluble Al: 0.022 mass % to 0.031 mass %; N: 0.003 mass % to 0.006 mass %; S and Se: 0.013 mass % to 0.022 mass % when converted into an S equivalent Seq represented by “[S]+0.405×[Se]” in which an S content is set as [S] and a Se content is set as [Se]; Mn: 0.045 mass % to 0.065 mass %; a Ti content being 0.005 mass % or less; and a balance being composed of Fe and inevitable impurities at 1280° C. to 1390° C., to make a substance functioning as an inhibitor to be solid-solved; next, hot-rolling the slab to obtain a steel strip; annealing the steel strip to form a primary inhibitor in the steel strip; next, cold-rolling the steel strip once or more; next, annealing the steel strip to perform decarburization and to cause primary recrystallization; next, performing nitriding treatment on the steel strip in a mixed gas of hydrogen, nitrogen and ammonia under a state where the steel strip is running to form a secondary inhibitor in the steel strip; and next, annealing the steel strip to cause secondary recrystallization. In the hot rolling, a ratio of N, contained in the slab, that is precipitated as AIN in the steel strip is set to 35% or less, and a ratio of S and Se, contained in the slab, that are precipitated as MnS or MnSe in the steel strip is set to 45% or less when converted into the S equivalent. The annealing to form the primary inhibitor in the steel strip is performed before a last-performed one of the cold rolling that is performed once or more. A rolling rate in the last-performed one of the cold rolling that is performed once or more is set to 84% to 92%. A circle-equivalent average grain diameter (diameter) of crystal grains obtained through the primary recrystallization is set to not less than 8 μm nor more than 15 μm. When a Mn content (mass %) in the slab is set as [Mn], a value A represented by an equation (1) satisfies an equation (2). When a N content (mass %) in the slab is set as [N], and an amount of N (mass %) in the steel strip that is increased by the nitriding treatment is set as ΔN, a value I represented by an equation (3) satisfies an equation (4).
[Mathematical expression 1]
A=([Mn]/54.9)/(Seq/32.1) equation (1)
1.6≦A≦2.3 equation (2)
[Mathematical expression 2]
I=1.3636×[Seq]/32.1+0.5337×[N]/14.0+0.7131×ΔN/14.0 equation (3)
0.0011≦I≦0.0017 equation (4)
According to the present invention, a composition of slab is appropriately defined, and further, conditions of hot rolling, cold rolling, annealing and nitriding treatment are also appropriately defined, so that it is possible to appropriately form a primary inhibitor and a secondary inhibitor. As a result of this, a texture obtained through secondary recrystallization is improved, which enables to stably obtain good magnetic properties.
A grain growth inhibiting effect provided by an inhibitor depends on an element, a size (form) and an amount of the inhibitor. Therefore, the grain growth inhibiting effect depends also on a method of forming the inhibitor.
Accordingly, in an embodiment of the present invention, a grain-oriented electrical steel sheet is manufactured while controlling a formation of inhibitor, in accordance with a flow chart shown in
A slab having a predetermined composition is heated (step S1), to make a substance functioning as an inhibitor to be solid-solved.
Next, hot rolling is performed, to thereby obtain a steel strip (hot-rolled steel strip) (step S2). In the hot rolling, fine AlN precipitates are formed.
Thereafter, the steel strip (hot-rolled steel strip) is annealed, in which precipitates such as AIN, MnS, Cu—S and MnSe (primary inhibitors) with proper sizes and amounts are formed (step S3).
Subsequently, the steel strip after annealed in step S3 (first annealed steel strip) is subjected to cold rolling (step S4). The cold rolling may be performed only once, or may also be performed in a plurality of times with an intermediate annealing therebetween. If the intermediate annealing is performed, it is also possible to omit the annealing in step S3 and to form the primary inhibitors in the intermediate annealing.
Next, the steel strip after the cold rolling is performed thereon (cold-rolled steel strip) is annealed (step S5). During the annealing, decarburization is carried out, and further, primary recrystallization is caused and an oxide layer a raw material for a glass film, a primary film or a forsterite film) is formed on a surface of the cold-rolled steel strip.
Thereafter, the steel strip after annealed in step S5 (second annealed steel strip) is subjected to nitriding treatment (step S6). Specifically, nitrogen is introduced into the steel strip. By this nitriding treatment, precipitates of AlN (secondary inhibitors) are formed.
Subsequently, an annealing separating agent is coated on surfaces of the steel strip after the nitriding treatment is performed thereon (nitrided steel strip), and after that, the steel strip is subjected to finish annealing (step S7). During the finish annealing, secondary recrystallization is induced.
(Composition of Slab)
Next, a composition of slab will be described.
C: 0.04 mass % to 0.09 mass %
When a C content is less than 0.04 mass %, it is not possible to achieve an appropriate texture obtained through the primary recrystallization. When the C content exceeds 0.09 mass %, the decarburization treatment (step S5) becomes difficult to be performed for preventing magnetic aging. Therefore, the C content is set to 0.04 mass % to 0.09 mass %.
Si: 2.5 mass % to 4.0 mass %
When a Si content is less than 2.5 mass %, good iron loss cannot be obtained. When the Si content exceeds 4.0 mass %, the cold rolling (step S4) becomes quite difficult to be performed. Therefore, the Si content is set to 2.5 mass % to 4.0 mass %.
Mn: 0.045 mass % to 0.065 mass %
When a Mn content is less than 0.045 mass %, a crack is likely to occur during the hot rolling (step S2), which decreases yield. Further, the secondary recrystallization (step S7) is not stabilized. When the Mn content exceeds 0.065 mass %, amounts of MnS and MnSe in the slab increase, so that there is a need to increase the temperature for heating the slab (step S1) in order to make MnS and MnSe to be appropriately solid-solved, which leads to an increase in cost and the like. Further, when the Mn content exceeds 0.065 mass %, a level at which Mn is solid-solved is likely to be non-uniform depending on positions, at the time of heating the slab (step S1). Therefore, the Mn content is set to 0.045 mass % to 0.065 mass %.
Acid-soluble Al: 0.022 mass % to 0.031 mass %
Acid-soluble Al bonds to N to form AlN. Further, AlN functions as a primary inhibitor and a secondary inhibitor. As described above, the primary inhibitor is formed during the annealing (step S3), and the secondary inhibitor is formed during the nitriding treatment (step S6). When an acid-soluble Al content is less than 0.022 mass %, a formation amount of AlN is insufficient, and further, the sharpness of the Goss orientation ({110}<001>) of crystal grains in a texture obtained through the secondary recrystallization (step S7) is deteriorated. When the acid-soluble Al content exceeds 0.031 mass %, there is a need to increase the temperature at the time of heating the slab (step S1) in order to achieve secure solid-solution of AlN. Therefore, the acid-soluble Al content is set to 0.022 mass % to 0.031 mass %.
N: 0.003 mass % to 0.006 mass %
N is important for forming AlN that functions as an inhibitor. However, when a N content exceeds 0.006 mass %, there is a need to set the temperature for heating the slab (step S1) to be higher than 1390° C. in order to achieve secure solid-solution. Further, the sharpness of the Goss orientation of crystal grains in a texture obtained through the secondary recrystallization (step S7) is deteriorated. When the N content is less than 0.003 mass %, AlN that functions as the primary inhibitor cannot be sufficiently precipitated, resulting in that the control of grain diameters of primary recrystallization grains obtained through the primary recrystallization (step S5) becomes difficult to be conducted. For this reason, the secondary recrystallization (step S7) becomes unstable. Therefore, the N content is set to 0.003 mass % to 0.006 mass %.
S, Se: 0.013 mass % to 0.022 mass % as S equivalent
S and Se bond to Mn and/or Cu, and compounds of S and Se with Mn and/or Cu function as the primary inhibitors. Further, the compounds thereof are also useful as precipitation nuclei of AIN. When an S content is set as [S] and a Se content is set as [Se], an S equivalent Seq of the content of S and Se is represented by “[S]+0.406×[Se]”, and when the content of S and Se exceeds 0.022 mass % when converted into the S equivalent Seq, there is a need to increase the temperature for heating the slab (step S1) in order to achieve secure solid-solution. When the content of S and Se is less than 0.013 mass % when converted into the S equivalent Seq, the primary inhibitors cannot be sufficiently precipitated (step S3), and the secondary recrystallization (step S7) becomes unstable. Therefore, the content of S and Se is set to 0.013 mass % to 0.022 mass % when converted into the S equivalent Seq.
Ti: 0.005 mass % or less
Ti bonds to N to form TiN. Further, when a Ti content exceeds 0.005 mass %, an amount of N that contributes to the formation of AlN becomes insufficient, resulting in that the primary inhibitors and the secondary inhibitors become insufficient. As a result of this, the secondary recrystallization (step S7) becomes unstable. Further, TiN remains even after the finish annealing (step S7) is performed, thereby deteriorating magnetic property (especially iron loss). Therefore, the Ti content is set to 0.005 mass % or less.
Cu: 0.05 mass % to 0.3 mass %
When the heating of slab (step S1) is performed at 1280° C. or higher, Cu forms fine precipitates together with S and Se (Cu—S, Cu—Se), and the precipitates function as inhibitors. Further, the precipitates also function as precipitation nuclei that make AlN functioning as the secondary inhibitor to be more uniformly dispersed. For this reason, the precipitates containing Cu contribute to the stabilization of secondary recrystallization (step S7). When a Cu content is less than 0.05 mass %, it is difficult to obtain these effects. When the Cu content exceeds 0.3 mass %, these effects saturate, and further, a surface flaw called “copper scab” may be generated at the time of hot rolling (step S2). Therefore, the Cu content is preferably 0.05 mass % to 0.3 mass %.
Sn, Sb: 0.02 mass % to 0.30 mass % in total
Sn and Sb are effective for improving the texture of the primary recrystallization (step S5). Further, Sn and Sb are grain boundary segregation elements, which stabilize the secondary recrystallization (step S7) and reduce the grain diameters of the crystal grains obtained through the secondary recrystallization. When a content of Sn and Sb is less than 0.02 mass % in total, it is difficult to obtain these effects. When the content of Sn and Sb exceeds 0.30 mass % in total, the cold-rolled steel strip is hard to be oxidized at the time of decarburization treatment (step S5), resulting in that the oxide layer is not sufficiently formed. Further, the decarburization is sometimes difficult to be performed. Therefore, the content of Sn and Sb is preferably 0.02 mass % to 0.30 mass % in total.
Note that P also exhibits the similar effect, but, it easily causes embrittlement. For this reason, a P content is preferably 0.020 mass % to 0.030 mass %.
Cr: 0.02 mass % to 0.30 mass %
Cr is effective for forming a good oxide layer at the time of decarburization treatment (step S5). The oxide layer contributes to the formation of glass film, which gives the surface tension on the grain-oriented electrical steel sheet. When a Cr content is less than 0.02 mass %, it is difficult to obtain this effect. When the Cr content exceeds 0.30 mass %, during the decarburization treatment (step S5), the cold-rolled steel strip is hard to be oxidized, resulting in that the oxide layer is not sufficiently formed and the decarburization is sometimes difficult to be performed. Therefore, the Cr content is preferably 0.02 mass % to 0.30 mass %.
It is also possible that other elements are contained for improving various properties of the grain-oriented electrical steel sheet. Further, a balance of the slab is preferably composed of Fe and inevitable impurities.
For example, Ni exhibits a significant effect for making the precipitates functioning as the primary inhibitors and the precipitates as the secondary inhibitors to be uniformly dispersed, and if an appropriate amount of Ni is contained, it becomes easy to obtain good and stable magnetic property. When a Ni content is less than 0.02 mass %, it is difficult to achieve this effect. When the Ni content exceeds 0.3 mass %, during the decarburization treatment (step S5), the cold-rolled steel strip is hard to be oxidized, resulting in that the oxide layer is not sufficiently formed and the decarburization is sometimes difficult to be performed.
Further, Mo and Cd form a sulfide or a selenide, and the precipitates thereof may function as inhibitors. When a content of Mo and Cd is less than 0.008 mass % in total amount, it is difficult to achieve this effect. When the content of Mo and Cd exceeds 0.3 mass % in total amount, the precipitates become coarse and thus do not function as the inhibitors, resulting in that the magnetic properties are not stabilized.
(Conditions of Manufacturing Procedure)
Next, conditions of respective manufacturing procedure shown in
Step S1
In step S1, heating of slab having the composition as described above is conducted. A method of obtaining the slab is not particularly limited. For example, it is possible to produce the slab through a continuous casting method. Further, it is also possible to adopt a breaking down (slabbing) method for easily conducting the heating of slab. By adopting the breaking down method, it is possible to reduce a carbon content. Concretely, a slab having an initial thickness of 150 mm to 300 mm, preferably 200 mm to 250 mm, is manufactured through the continuous casting method. Further, it is also possible to produce a so-called thin slab by setting the initial thickness of the slab to about 30 mm to 70 mm. When the thin slab method is adopted, it becomes possible to simplify or omit rough rolling to an intermediate thickness at the time of hot rolling (step S2).
A temperature for heating the slab is set to a temperature at which a substance functioning as an inhibitor in the slab is solid-solved (made into solution), which is, for example, 1280° C. or higher. As the substance functioning as the inhibitor, AlN, MnS, MnSe, Cu—S and the like can be cited. If a slab is heated at a temperature lower than the temperature at which the substance functioning as the inhibitor in the slab is solid-solved, the substance is precipitated non-uniformly, which sometimes leads to a generation of so-called skid mark in the final product.
Note that an upper limit of the temperature for heating the slab is not particularly limited in terms of metallurgy. However, if the heating of slab is conducted at 1390° C. or higher, various difficulties regarding facilities and operations may arise. For this reason, the heating of slab is conducted at 1390° C. or lower.
A method of heating the slab is not particularly limited. For instance, it is possible to adopt methods of gas heating, induction heating, direct current heating and the like. Further, in order to easily conduct heating in these methods, it is also possible to perform breakdown on the casting slab. Further, if the temperature for heating the slab is set to 1300° C. or higher, it is also possible to use the breakdown to improve the texture to reduce the amount of carbon.
Step S2
In step S2, the slab after being heated is hot-rolled, thereby obtaining a hot-rolled steel strip.
At this time, a ratio of N, contained in the slab, that is precipitated as AlN in the hot-rolled steel strip (precipitation rate of N) is set to 35% or less. When the precipitation rate of N exceeds 35%, precipitates, which are coarse after the annealing (step S3) and do not function as the primary inhibitors, increase, and thus fine precipitates functioning as the primary inhibitors become insufficient. When such fine precipitates (primary inhibitors) are insufficient, the secondary recrystallinity (step S7) becomes unstable.
Note that the precipitation rate of N can be adjusted by a cooling condition in the hot rolling. Specifically, if a temperature at which cooling is started is set high and a cooling rate is also set quick, the precipitation rate is reduced. A lower limit of the precipitation rate is not particularly limited, but, it is difficult to set the ratio to less than 3%.
Further, a ratio of S and/or Se, contained in the slab, that are/is precipitated as MnS or MnSe in the hot-rolled steel strip (precipitation rate of S and Se as compounds with Mn) is set to 45% or less as the S equivalent Seq. When the precipitation rate of S and Se as compounds with Mn exceeds 45% as the S equivalent, the precipitation at the time of hot rolling becomes non-uniform. Further, the precipitates become coarse and difficult to function as effective inhibitors in the secondary recrystallization (step S7).
Step S3
In step S3, the hot-rolled steel strip is annealed, and precipitates such as AlN, MnS and MnSe (primary inhibitors) are formed.
This annealing is performed to uniformize the non-uniform structure in the hot-rolled steel strip mainly generated during the hot rolling, to precipitate the primary inhibitors and to disperse the inhibitors in a fine form. Note that the condition at the time of annealing is not particularly limited. For instance, a condition described in Patent Document 17, Patent Document 18,
Further, a cooling condition in the annealing is not particularly limited, but, it is preferable to set a cooling rate from 700° C. to 300° C. to 10° C./second or more, in order to securely achieve fine primary inhibitors and to secure a quenched hard phase.
Note that if Cu is contained in the slab, a ratio of S and/or Se, contained in the steel strip after the annealing, that are/is precipitated as Cu—S or Cu—Se (precipitation rate of S and Se as compounds with Cu) is preferably set to 25% to 60% as the S equivalent Seq. The precipitation rate of S and Se as compounds with Cu often becomes less than 25% when the cooling in the annealing is conducted at a very fast speed. Further, when the cooling in the annealing is performed at a very fast speed, the precipitation of primary inhibitors often becomes insufficient. Accordingly, when the precipitation rate of S and Se as compounds with Cu is less than 25%, the secondary recrystallization (step S7) is likely to be unstable. When the precipitation rate of S and Se as compounds with Cu exceeds 60%, the number of coarse precipitates is large, resulting in that fine precipitates functioning as the primary inhibitors are likely to be insufficient. For this reason, the secondary recrystallization (step S7) is likely to be unstable.
Step S4
In step S4, the annealed steel strip is cold-rolled, thereby obtaining a cold-rolled steel strip.
The number of times of cold rolling is not particularly limited. Note that if the cold rolling is performed only once, the annealing of the hot-rolled steel strip (step S3) is performed before the cold rolling as an annealing before final cold rolling. Further, if a plurality of times of cold rolling are performed, it is preferable that an intermediate annealing is conducted between the processes of cold rolling. If the plurality of times of cold rolling is performed, it is also possible to omit the annealing in step S3 and form the primary inhibitors in the intermediate annealing.
Further, a rolling rate in the last-performed one of the cold rolling (final cold rolling) is set to 84% to 92%. When the rolling rate at the time of final cold rolling is less than 84%, the sharpness of the Goss orientation in the primary recrystallization texture obtained through the annealing (step S5) is broad, and further, the intensity in the Σ9 coincident orientation of Goss becomes weak. As a result of this, high magnetic flux density cannot be obtained. When the rolling rate at the time of final cold rolling exceeds 92%, the number of crystal grains of the Goss orientation in the texture obtained through the primary recrystallization (step S5) becomes extremely small, resulting in that the secondary recrystallization (step S7) becomes unstable.
The condition of the final cold rolling is not particularly limited. For instance, the final cold rolling may also be conducted at room temperature. Further, if a temperature during at least one pass is maintained in a range of 100° C. to 300° C. for one minute or more, the texture obtained through the primary recrystallization (step S5) is improved, and quite good magnetic property is provided. This is described in Patent Document 19 and the like.
Step S5
In step S5, the cold-rolled steel strip is annealed, and during this process of annealing, decarburization is performed to cause the primary recrystallization. Further, as a result of performing the annealing, an oxide layer is formed on a surface of the cold-rolled steel strip. An average grain diameter (diameter of circle-equivalent area) of crystal grains obtained through the primary recrystallization is set to not less than 8 μm nor more than 15 μm. When the average grain diameter of the primary recrystallization grains is less than 8 μm, a temperature at which the secondary recrystallization occurs during the finish annealing (step S7) becomes quite low. Specifically, the secondary recrystallization occurs at a low temperature. As a result of this, the sharpness of the Goss orientation is deteriorated. When the average grain diameter of the primary recrystallization grains exceeds 15 μm, a temperature at which the secondary recrystallization occurs during the finish annealing (step S7) becomes high. As a result of this, the secondary recrystallization (step S7) becomes unstable. Note that if the temperature for heating the slab (step S1) is set to 1280° C. or higher to make the substance functioning as the inhibitor to be completely solid-solved, the average grain diameter of the primary recrystallization grains becomes approximately not less than 8 μm nor more than 15 μm even if the temperature at the time of annealing before final cold rolling (step S3) and the temperature at the time of annealing (step S5) are changed.
In terms of grain growth, the smaller the primary recrystallization grains, the larger the absolute number of crystal grains of the Goss orientation to be nuclei for the secondary recrystallization, at the stage of primary recrystallization. For instance, if the average grain diameter of the primary recrystallization grains is not less than 8 μm nor more than 15 μm, the absolute number of crystal grains of the Goss orientation is about five times more than that in a case where the average grain diameter of the primary recrystallization grains after the decarburization annealing is completed is 18 μm to 35 μm (Patent Document 20). Further, the smaller the primary recrystallization grains, the smaller the crystal grains obtained through the secondary recrystallization (secondary recrystallization grains). By these synergistic effects, iron loss of the grain-oriented electrical steel sheet is ameliorated, and further, crystal grains oriented in the Goss orientation are selectively grown, resulting in that magnetic flux density is improved.
The condition during the annealing in step S5 is not particularly limited, and a conventional one may also be used. For instance, it is possible to perform annealing at 650° C. to 950° C. for 80 seconds to 500 seconds in a wet atmosphere of mixed nitrogen and hydrogen. It is also possible to adjust a period of time and the like in accordance with a thickness of the cold-rolled steel strip. Further, it is preferable that a heating rate from the start of the temperature rise up to 650° C. or higher is set to 100° C./second or more. This is because the primary recrystallization texture is improved and better magnetic property is provided. A method of conducting heating at 100° C./second or more is not particularly limited, and, for instance, methods of resistance heating, induction heating, directly energy input heating and the like can be employed.
If the heating rate is increased, the number of crystal grains of the Goss orientation in the primary recrystallization texture becomes large, and the secondary recrystallization grains become small. This effect can also be achieved when the heating rate is around 100° C./second, but, it is more preferable to set the heating rate to 150° C./second or more.
Step S6
In step S6, nitriding treatment is performed on the steel strip after the primary recrystallization. In the nitriding treatment, N that bonds to the acid-soluble Al is introduced into the steel strip, to thereby form the secondary inhibitors. At this time, if the introduction amount of N is too small, the secondary recrystallization (step S7) becomes unstable. If the introduction amount of N is too large, the sharpness of the Goss orientation is quite deteriorated, and further, a glass film defect in which a base iron is exposed often occurs. Accordingly, conditions as described below are set on the introduction amount of N.
Regarding the contents of Mn, S and Se in the slab, a value A defined by an equation (1) satisfies an equation (2). Here, [Mn] represents the Mn content.
[Mathematical expression 3]
A=([Mn]/54.9)/(Seq/32.1) equation (1)
1.6≦A≦2.3 equation (2)
Further, a value I defined by an equation (3) satisfies an equation (4). Here, [N] represents the N content in the slab, and ΔN represents an increasing amount of the N content in the nitriding treatment.
[Mathematical expression 4]
I=1.3636×[Seq]/32.1+0.5337×[N]/14.0+0.7131×ΔN/14. equation (3)
0.0011≦I≦0.0017 equation (4)
If such conditions are satisfied, the secondary inhibitors are appropriately formed, the secondary recrystallization (step S7) is stabilized, and the texture having a superior sharpness of the Goss orientation can be obtained.
When the value A is less than 1.6, the secondary recrystallization (step S7) becomes unstable. When the value A exceeds 2.3, it is not possible to make the substance functioning as the inhibitor to be solid-solved, unless the temperature for heating the slab (step S1) is set extremely high (set to higher than 1390° C.)
When the value I is less than 0.0011, the total amount of inhibitors is insufficient, resulting in that the secondary recrystallization (step S7) becomes unstable. When the value I exceeds 0.0017, the total amount of inhibitors becomes too much, which deteriorates the sharpness of the Goss orientation in the texture in the secondary recrystallization (step S7), and it becomes difficult to achieve good magnetic property.
Note that the amount of N contained in the steel strip after the nitriding treatment is preferably greater than the amount of N that forms AlN. This is for realizing the stabilization of secondary recrystallization (step S7). Although it is not clarified why such a N content enables the stabilization of secondary recrystallization (step S7), the reason can be estimated as follows. In the finish annealing (step S7), since the temperature of the steel strip becomes high, AlN functioning as the secondary inhibitor is sometimes decomposed or solid-solved. This phenomenon occurs as denitrification since N is more easily diffused than aluminum. For this reason, the denitrification is facilitated as the amount of N contained in the steel strip after the niriding treatment is smaller, resulting in that an action of the secondary inhibitor easily disappears in an early stage. This denitrification becomes hard to occur when the amount of N contained in the steel strip after the nitriding treatment is greater than the amount of N that forms AlN. Thereby, the decomposition and solid-solution of AlN become hard to occur. Therefore, a sufficient amount of AlN functions as the secondary inhibitors. Further, when adjusting the amount of N as described above, it is preferable to take the equations (3) and (4) into consideration.
Note that when a large amount of Ti is contained in the steel strip (for instance, when the Ti content exceeds 0.005 mass %), a large amount of TiN is formed in the nitriding treatment, and is remained even after the finish annealing (step S7) is performed, so that magnetic property (particularly, iron loss) is sometimes deteriorated.
A method in the nitriding treatment is not particularly limited, and there can be cited a method in which nitrides (CrN and MnN, and the like) are mixed in an annealing separating agent and nitriding is performed in high-temperature annealing, and a method in which a strip (steel strip) is nitrided, while being running, in a mixed gas of hydrogen, nitrogen and ammonia. The latter method is preferable in terms of industrial production.
Further, the nitriding treatment is preferably performed on both surfaces of the steel strip after the primary recrystallization. In the present embodiment, the grain diameter of the primary recrystallization grain is about not less than 8 μm nor more than 15 μm and the N content in the slab is 0.003 mass % to 0.006 mass %. Accordingly, the temperature at which the secondary recrystallization (step S7) is started is low to be 1000° C. or lower. Therefore, in order to obtain the superior texture of the Goss orientation through the secondary recrystallization, it is preferable that the inhibitors uniformly disperse along the entire thickness direction. For this reason, N is preferably diffused in the steel strip in an early stage, and the nitriding treatment is preferably performed substantially equally on both surfaces of the steel strip.
For example, if a nitrogen content of a 20% thickness portion of one surface of the steel strip is set as σN1 (mass %), and a nitrogen content of a 20% thickness portion of the other surface of the steel strip is set as σN2 (mass %), a value B defined by an equation (5) preferably satisfies an equation (6).
[Mathematical expression 5]
B=|σN1−σN2|/ΔN equation (5)
B≦0.35 equation (6)
In the present embodiment, the primary recrystallization grain is small and the temperature at which the secondary recrystallization (step S7) is started is low, so that when the value B exceeds 0.35, the secondary recrystallization is started before N is diffused in the entire steel strip, resulting in that the secondary recrystallization becomes unstable. Further, since N is not diffused uniformly in the thickness direction, the nuclei for the secondary recrystallization are generated at positions separated from a surface layer portion, resulting in that the sharpness of the Goss orientation deteriorates.
Here, a nitriding furnace suitably employed in the nitriding treatment in step S6 will be described.
As shown in
[Mathematical expression 6]
t1≧50 mm equation (7)
1≦t1 equation (8)
t2≧2×t1 equation (9)
t3≧2.5×t1 equation (10)
L≧1.2×W equation (11)
When the nitriding treatment is conducted by using such a nitriding furnace, almost no variation in the ammonia concentration occurs in the furnace shell 3, and it is possible to easily reduce the value B to 0.35 or less. Note that in the example shown in
Note that it is also possible that a plurality of the pipes 1 shown in
Further, the pipe 1 may also be divided into a plurality of units. For example, it is also possible that three pipe units 1a formed by dividing the pipe 1 are provided, as shown in
Note that a distance L0 between adjacent pipe units 1a in the running direction of the strip 11 is preferably 550 mm or less. When the distance L0 exceeds 550 mm, the level of nitriding in the width direction of the strip is likely to be non-uniform, resulting in that the secondary recrystallization is likely to be non-uniform.
Further, it is also possible that the introduction of ammonia gas into the furnace shell 3 is performed through inlet ports 4 provided to wall portions of the furnace shell 3, as shown in
[Mathematical expression 7]
t3≧W/3 equation (12)
t4≧100 mm equation (13)
H≦W/3 equation (14)
By conducting the nitriding treatment using such a nitriding furnace, it is possible to easily reduce the value B to 0.35 or less.
The inlet ports 4 are preferably provided on both sides in the width direction of the strip 11. This is for easily enabling the concentration of ammonia gas in the furnace shell 3 to be more uniform. Further, in order to realize more uniform nitriding, the inlet ports 4 are preferably provided at substantially the same height as the strip 11, but, it is possible to perform generally good nitriding as long as the equation (14) is satisfied.
Note that in the examples shown in
Step S7
In step S7, the finish annealing after coating an annealing separating agent whose main component is, for instance, MgO (annealing separating agent containing 90 mass % or more of MgO, for example) is performed, to thereby cause the secondary recrystallization.
At this time, the primary inhibitors (AlN, MnS, MnSe and Cu—S formed in step S3) and the secondary inhibitors (AlN formed in step S6) control the secondary recrystallization. Specifically, with the use of the primary inhibitors and the secondary inhibitors, preferred growth in the Goss orientation in the thickness direction is facilitated, resulting in that magnetic property is remarkably improved. Further, the secondary recrystallization is started at a position close to the surface layer of the steel strip. Further, in the present embodiment, amounts of the primary inhibitors and the secondary inhibitors are appropriately set, and the grain diameter of the primary recrystallization grain is about not less than 8 μm nor more than 15 μm. For this reason, the driving force for grain boundary migration (grain growth: secondary recrystallization) becomes large, resulting in that the secondary recrystallization is started in a further early stage of the stage of temperature rise (at a lower temperature) in the finish annealing. Further, the selectivity of the second recrystallization grains of the Goss orientation in the thickness direction of the steel strip is increased. As a result of this, the sharpness of the Goss orientation of the texture obtained through the secondary recrystallization becomes superior. Specifically, the secondary recrystallization stably occurs, resulting in that good magnetic property can be achieved.
Further, the finish annealing for the secondary recrystallization is performed in a box-type annealing furnace, for example. At this time, the steel strip after the nitriding treatment is in a coil shape and has a limited weight (size). In order to improve productivity in such finish annealing, it can be considered to increase the weight per coil. However, if the weight of the coil is increased, a temperature hysteresis is likely to largely differ among positions of the coil. Particularly, since a maximum temperature in the finish annealing is limited because of the specification of the facility, when the temperature at which the secondary recrystallization is started becomes high, a difference in the temperature hysteresis between a coldest point and a hottest point in the coil becomes significantly large. Therefore, the secondary recrystallization is preferably started at a time at which the difference in the temperature hysteresis is hardly generated, namely, at a time of temperature rise. If the secondary recrystallization is started at the time of temperature rise, the non-uniformity of magnetic property between the positions on the coil is significantly reduced, the annealing condition is easily set, and the magnetic property is quite highly stabilized. In the present embodiment, the temperature at which the secondary recrystallization is started becomes relatively low, which is also effective in an actual operation.
After conducting step S7, a coating of an insulation tension coating, a flattening treatment and the like are performed, for instance.
According to the present embodiment, it is possible to improve the state of inhibitors to obtain good magnetic property. As important indexes of magnetic property in the grain-oriented electrical steel sheet, there can be cited iron loss, magnetic flux density and magnetostriction. When the sharpness of the Goss orientation and the magnetic flux density are high, the iron loss can be improved utilizing magnetic domain control technology. The magnetostriction can be reduced (improved) when the magnetic flux density is high. When the magnetic flux density in the grain-oriented electrical steel sheet is high, it is possible to relatively reduce an exciting current in a transformer manufactured with the grain-oriented electrical steel sheet, so that the transformer can be made smaller in size.
As above, the magnetic flux density is important magnetic property in the grain-oriented electrical steel sheet. Further, according to the present embodiment, it is possible to stably manufacture a grain-oriented electrical steel sheet whose magnetic flux density (B8) is 1.92 T or more. Here, the magnetic flux density (B8) corresponds to one in a magnetic field of 800 A/m.
Note that regarding the production of slab, a thin slab casting and a steel strip casting (strip caster) have been put into practical use in recent years, as technology to supplement ordinary continuous hot rolling, and it is also possible to conduct these castings. However, in these castings, so-called “center segregation” occurs at the time of solidification, and it is quite difficult to obtain a good uniform solid-solution state. Accordingly, when these castings are employed, in order to obtain a good uniform solid-solution state, it is preferable to perform solid-solution heat treatment before conducting the hot rolling (step S2).
Slabs each composed of components shown in Table 1 were melted and the slabs were heated at 1300° C. to 1350° C. (step S1).
Next, hot rolling was conducted (step S2), thereby obtaining hot-rolled steel strips each having a thickness of 2.3 mm. Regarding the hot rolling, in order to suppress the precipitation of substances functioning as inhibitors (AlN, MnS, Cu—S and MnSe) as much as possible, finish hot rolling was started at a temperature exceeding 1050° C., and after the completion of finish hot rolling, quick cooling was performed. Thereafter, the hot-rolled steel strips were subjected to continuous annealing at 1120° C. for 60 seconds, and were cooled at 20° C./second (step S3). Subsequently, the steel strips were subjected to cold rolling at 200° C. to 250° C., thereby obtaining cold-rolled steel strips each having a thickness of 0.285 mm (step S4). Next, the steel strips were heated up to 800° C. at 180° C./second, heated from 800° C. up to 850° C. at about 20° C./second, and annealed, for decarburization and primary recrystallization, at 850° C. for 150 seconds in a mixed atmosphere of H2 and N2 at a dew point of 65° C. (step S5). Thereafter, nitriding treatment was performed on the steel strips, while running the strips (steel strips), in an ammonia atmosphere in which ammonia was introduced from directions above and below the strips (step S6). At this time, an introduction amount of ammonia introduced into the atmosphere was changed in various ways to change an amount of nitriding.
Subsequently, an annealing separating agent having MgO as its main component was coated on both surfaces of the steel strips after the nitriding treatment, and finish annealing was conducted to cause secondary recrystallization (step S7). Specifically, secondary recrystallization annealing was performed. The finish annealing was conducted in an atmosphere in which a ratio of N2 was 25 vol % and a ratio of H2 was 75 vol %, and a temperature of the steel strips was raised up to 1200° C. at 10° C./hour to 20° C./hour. Next, purification treatment was performed at a temperature of 1200° C. for 20 hours or more, in an atmosphere in which a ratio of H2 was 100 vol %. Further, a coating of an insulation tension coating, and a flattening treatment were performed.
In such a series of treatment processes, various precipitation rates and increasing amounts of nitriding and magnetic properties in the obtained grain-oriented electrical steel sheets were measured. Results thereof are shown in Table 2.
As shown in Table 2, in examples Nos. 3, 4, 7, 8, 9 and 10, high magnetic properties, especially, high magnetic flux density (B8) were obtained.
Slabs each composed of components shown in Table 3 were melted and the slabs were heated at 1200° C. to 1340° C. (step S1).
Next, cold-rolled steel strips were obtained in the same manner as the experimental example 1 (steps S2 to S4). After that, the steel strips were heated up to 800° C. at 180° C./second, heated from 800° C. up to 850° C. at about 20° C./second, and annealed, for decarburization and primary recrystallization, at 850° C. for 150 seconds in a mixed atmosphere of H2 and N2 at a dew point of 65° C. (step S5). Subsequently, the steel strips were subjected to nitriding treatment (step S6). At this time, an introduction amount of ammonia introduced into an atmosphere was changed in various ways to change an amount of nitriding. Further, regarding the steel strips in Nos. 11 to 20, the nitriding treatment was performed on the steel strips, while running the strips (steel strips), in an ammonia atmosphere in which ammonia was introduced from directions above and below the strips, in the same manner as the experimental example 1. Further, regarding the steel strips in Nos. 21 to 29, the nitriding treatment was performed on the steel strips, while running the strips (steel strips), in an ammonia atmosphere in which ammonia was introduced only from a direction above the strips.
Subsequently, an annealing separating agent having MgO as its main component was coated on both surfaces of the steel strips after the nitriding treatment, and finish annealing was conducted to cause secondary recrystallization (step S7). Specifically, secondary recrystallization annealing was performed. The finish annealing was conducted in an atmosphere in which a ratio of N2 was 25 vol % and a ratio of H2 was 75 vol %, and a temperature of the steel strips was raised up to 1200° C. at 10 to 20° C./hour.
In such a series of treatment processes, various precipitation rates and increasing amounts of nitriding and magnetic properties in the obtained grain-oriented electrical steel sheets were measured. Results thereof are shown in Table 4.
As shown in Table 4, in examples Nos. 15, 16, 17, 23, 26, 27, 28 and 29, high magnetic properties, especially, high magnetic flux density (B8) were obtained. In particular, higher magnetic properties were obtained in the examples Nos. 15 to 17, in which ammonia was introduced from the directions above and below the strips.
Slabs each composed of components shown in Table 5 were melted and the slabs were heated at 1230° C. to 1350° C. (step S1).
Next, hot rolling was conducted (step S2), thereby obtaining hot-rolled steel strips each having a thickness of 2.3 mm. Regarding the hot rolling, in order to suppress the precipitation of substances functioning as inhibitors (AlN, MnS, Cu—S and MnSe) as much as possible, finish hot rolling was started at a temperature exceeding 1050° C., and after the finish hot rolling, quick cooling was performed. Thereafter, continuous annealing was performed on the hot-rolled steel strips at 1120° C. for 30 seconds, further performed at 930° C. for 60 seconds, and the steel strips were cooled at 20° C./second (step S3). Subsequently, the steel strips were subjected to cold rolling at 200° C. to 250° C., thereby obtaining cold-rolled steel strips each having a thickness of 0.22 mm (step S4). Next, the steel strips were heated up to 800° C. at 200° C./second, heated from 800° C. up to 850° C. at about 20° C./second, and annealed, for decarburization and primary recrystallization, at 850° C. for 110 seconds in a mixed atmosphere of H2 and N2 at a dew point of 65° C. (step S5). Thereafter, nitriding treatment was performed on the steel strips, while running the strips (steel strips), in an ammonia atmosphere in which ammonia was introduced from directions above and below the strips (step S6). At this time, an introduction amount of ammonia introduced into the atmosphere was changed in various ways to change an amount of nitriding.
Subsequently, an annealing separating agent having MgO as its main component was coated on both surfaces of the steel strips after the nitriding treatment, and finish annealing was conducted to cause secondary recrystallization (step S7). Specifically, secondary recrystallization annealing was performed. The finish annealing was conducted in an atmosphere in which a ratio of N2 was 25 vol % and a ratio of H2 was 75 vol %, and a temperature of the steel strips was raised up to 1200° C. at 10° C./hour to 20° C./hour. Next, purification treatment was performed at a temperature of 1200° C. for 20 hours or more, in an atmosphere in which a ratio of H2 was 100 vol %. Further, a coating of an insulation tension coating, and a flattening treatment were performed.
In such a series of treatment processes, various precipitation rates and increasing amounts of nitriding and magnetic properties in the obtained grain-oriented electrical steel sheets were measured. Results thereof are shown in Table 6.
As shown in Table 6, in examples Nos. 32, 33, 34, 37, 38, 39 and 40, high magnetic properties, especially, high magnetic flux density (B8) were obtained.
Slabs each composed of components shown in Table 7 were melted and the slabs were heated at 1200° C. to 1340° C. (step S1).
Next, cold-rolled steel strips were obtained in the same manner as the experimental example 3 (steps S2 to S4). After that, the steel strips were heated up to 800° C. at 200° C./second, heated from 800° C. up to 850° C. at about 20° C./second, and annealed, for decarburization and primary recrystallization, at 850° C. for 110 seconds in a mixed atmosphere of H2 and N2 at a dew point of 65° C. (step S5). Subsequently, the steel strips were subjected to nitriding treatment (step S6). At this time, an introduction amount of ammonia introduced into an atmosphere was changed in various ways to change an amount of nitriding. Further, regarding the steel strips in Nos. 41 to 50, the nitriding treatment was performed on the steel strips, while running the strips (steel strips), in an ammonia atmosphere in which ammonia was introduced from directions above and below the strips, in the same manner as the experimental example 1. Further, regarding the steel strips in Nos. 51 to 60, the nitriding treatment was performed on the steel strips, while running the strips (steel strips), in an ammonia atmosphere in which ammonia was introduced only from a direction above the strips.
Subsequently, an annealing separating agent having MgO as its main component was coated on both surfaces of the steel strips after the nitriding treatment, and finish annealing was conducted to cause secondary recrystallization (step S7). Specifically, secondary recrystallization annealing was performed. The finish annealing was conducted in an atmosphere in which a ratio of N2 was 25 vol % and a ratio of H2 was 75 vol %, and a temperature of the steel strips was raised up to 1200° C. at 10 to 20° C./hour.
In such a series of treatment processes, various precipitation rates and increasing amounts of nitriding and magnetic properties in the obtained grain-oriented electrical steel sheets were measured. Results thereof are shown in Table 8.
As shown in Table 8, in examples Nos. 45, 46, 47, 52, 53, 55, 56, 58, 59 and 60, high magnetic properties, especially, high magnetic flux density (B8) were obtained. In particular, higher magnetic properties were obtained in the examples Nos. 45 to 47, in which ammonia was introduced from the directions above and below the strips.
The increasing amount of N content in the nitriding treatment (step S6) performed on the steel strips obtained from the slabs in the examples No. 3, No. 4 of the experimental example 1 was set to 0.010 mass % to 0.013 mass %. Further, in the nitriding treatment, the introduction amount of ammonia introduced above and below the running strips (steel strips) was adjusted and the value B was changed in various ways. After that, grain-oriented electrical steel sheets were manufactured in the same manner as the experimental example 1. Further, a relation between the value B and the magnetic flux density (B8) was examined. Results thereof are shown in
As shown in
The increasing amount of N content in the nitriding treatment (step S6) performed on the steel strips obtained from the slabs in the examples No. 33, No. 34 of the experimental example 3 was set to 0.009 mass % to 0.012 mass %. Further, in the nitriding treatment, the introduction amount of ammonia introduced above and below the running strips (steel strips) was adjusted and the value B was changed in various ways. After that, grain-oriented electrical steel sheets were manufactured in the same manner as the experimental example 3. Further, a relation between the value B and the magnetic flux density (B8) was examined. Results thereof are shown in
As shown in
Industrial Applicability
The present invention can be utilized in an industry of manufacturing grain oriented electrical steel sheets and an industry in which grain oriented electrical steel sheets are used.
| Number | Date | Country | Kind |
|---|---|---|---|
| 2008-232569 | Sep 2008 | JP | national |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/JP2009/065682 | 9/8/2009 | WO | 00 | 2/24/2011 |
| Publishing Document | Publishing Date | Country | Kind |
|---|---|---|---|
| WO2010/029921 | 3/18/2010 | WO | A |
| Number | Name | Date | Kind |
|---|---|---|---|
| 3933024 | Matsumoto et al. | Jan 1976 | A |
| 4623406 | Suga et al. | Nov 1986 | A |
| 4623407 | Suga et al. | Nov 1986 | A |
| 4753692 | Kuroki et al. | Jun 1988 | A |
| 4806176 | Harase et al. | Feb 1989 | A |
| 4863532 | Kuroki et al. | Sep 1989 | A |
| 4898626 | Shoen et al. | Feb 1990 | A |
| 4979996 | Kobayashi et al. | Dec 1990 | A |
| 5215603 | Nakayama et al. | Jun 1993 | A |
| 5643370 | Huppi | Jul 1997 | A |
| 5759293 | Takahashi et al. | Jun 1998 | A |
| 5779819 | Huppi | Jul 1998 | A |
| 6432222 | Ohata et al. | Aug 2002 | B2 |
| 6451128 | Lee et al. | Sep 2002 | B1 |
| 7833360 | Kumano et al. | Nov 2010 | B2 |
| 7857915 | Kumano et al. | Dec 2010 | B2 |
| 8097094 | Murakami | Jan 2012 | B2 |
| 20020007870 | Ohata et al. | Jan 2002 | A1 |
| 20020011278 | Komatsubara et al. | Jan 2002 | A1 |
| 20070062611 | Murakami | Mar 2007 | A1 |
| 20090032142 | Kumano et al. | Feb 2009 | A1 |
| 20090044881 | Kumano et al. | Feb 2009 | A1 |
| Number | Date | Country |
|---|---|---|
| 0947597 | Jan 2005 | EP |
| 40-15644 | Jul 1965 | JP |
| 50-16610 | Feb 1975 | JP |
| 57-198214 | Dec 1982 | JP |
| 58-23414 | Feb 1983 | JP |
| 59-56522 | Apr 1984 | JP |
| 60-218426 | Jan 1985 | JP |
| 60-177131 | Sep 1985 | JP |
| 1-290716 | Nov 1989 | JP |
| 2-182866 | Jul 1990 | JP |
| 5-112827 | May 1993 | JP |
| 7-252532 | Oct 1995 | JP |
| 7-305116 | Nov 1995 | JP |
| 8-253815 | Jan 1996 | JP |
| 8-279408 | Oct 1996 | JP |
| 9-118964 | May 1997 | JP |
| 11-21627 | Jan 1999 | JP |
| 2000-199015 | Jul 2000 | JP |
| 2001-152250 | Jun 2001 | JP |
| 2005-226111 | Aug 2005 | JP |
| 2007-238984 | Sep 2007 | JP |
| WO 2006132095 | Dec 2006 | WO |
| Number | Date | Country | |
|---|---|---|---|
| 20110155285 A1 | Jun 2011 | US |
