CA2081496C - Method of manufacturing a cold rolled steel sheet exhibiting an excellent resistance to cold-work embrittlement and a small planar anisotropy - Google Patents
Method of manufacturing a cold rolled steel sheet exhibiting an excellent resistance to cold-work embrittlement and a small planar anisotropyInfo
- Publication number
- CA2081496C CA2081496C CA 2081496 CA2081496A CA2081496C CA 2081496 C CA2081496 C CA 2081496C CA 2081496 CA2081496 CA 2081496 CA 2081496 A CA2081496 A CA 2081496A CA 2081496 C CA2081496 C CA 2081496C
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- steel sheet
- rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0426—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
- C21D8/0473—Final recrystallisation annealing
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- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
A method of manufacturing a cold rolled steel sheet includes the steps of preparing, as a material, a steel whose composition consists of C : 0.004 wt% or less, Si : 0.10 wt% or less, Mn : 0.50 wt% or less, Ti : between 0.01 wt% and 0.10 wt%, Nb : between 0.003 wt% and 0.03 wt%, B : between 0.001 wt% and 0.004 wt%, Al : between 0.03 wt% and 0.10 wt%, P : 0.025 wt% or less, S :0.01 wt%
or less, N : 0.006 wt% or less; performing a hot rolling on the material steel under the conditions of a finishing temperature between 800°C and 900°C; coiling the material at a temperature lower than 650°C; performing a cold rolling; performing a continuous annealing at a temperature between 830°C and Ac3 transformation point;
and performing a skin pass rolling.
or less, N : 0.006 wt% or less; performing a hot rolling on the material steel under the conditions of a finishing temperature between 800°C and 900°C; coiling the material at a temperature lower than 650°C; performing a cold rolling; performing a continuous annealing at a temperature between 830°C and Ac3 transformation point;
and performing a skin pass rolling.
Description
20811~
BACKGROUND OF THE INVENTION
Field of the Invention The present invention relates to a method of manufacturing a cold rolled steel sheet that exhibits excellent resistance to cold-work embrittlement and a small planar anisotropy by the continuous annealing method which is suitable as a pressed steel sheet for use in automobiles.
Description of the Related Art When a cold rolled steel sheet is manufactured, a continuous annealing, including heating and cooling which last for a short period of time, is generally conducted subsequent to the cold rolling. In this continuous annealing process, the material quality of the product is greatly affected by the chemical composition of the material. Hence, to obtain a steel sheet exhibiting excellent deep drawing property and stretchability, it has been the practice to add a carbide/nitride producing component, such as Ti or Nb, to the extra low carbon steel.
However, the steel sheet in which Ti or Nb is present is characterized in that Ti is readily combined with C, S, N or O in the steel to form a precipitate.
Consequently, the grain boundary is cleaned and the grain boundary strength is thus greatly reduced, increasing the 2~81496 possibility that a brittle fracture (the fracture due to cold-work embrittlement) will occur after deep drawing.
Also, it has been a practice to obtain a high-strength steel sheet by adding Mn, Si or P to the steel material.
In that case, however, since Si and P readily embrittle the steel sheet, the resistance to cold-work embrittlement greatly deteriorates. To improve such a drawback, B has been added to the steel in the form of a solid solution to increase the grain boundary strength, like C.
However, it is well known that adding B deteriorates the formability. Therefore, the proportion of B to be added is restricted to such a small value that sufficient resistance to cold-work embrittlement cannot be obtained.
Various other methods of improving the deep drawing property and stretchability of the steel sheet by controlling the conditions of hot rolling, cold rolling or annealing during the manufacturing process of the steel sheet have also been suggested. Generally, the hot rolling finishing temperature is set to an Ar3 transformation point or above from the viewpoint of improving the deep drawing property. The coiling temperature is between 650 and 800C from the viewpoint of improving the formability, especially deep drawing properties. The annealing temperature is set to a 208 ~ 496 relatively low temperature which is equal to or higher than the recrystallization temperature and which is effective in terms of the energy.
Unexamined Japanese Patent Publication No.
62-278232 (published December 3, 1987) discloses a method of manufacturing a cold rolled steel sheet of the aforementioned type for use in non-aging deep drawing by the direct hot-rolling method. Unexamined Japanese Patent Publication No.
1-177321 (published July 13, 1989) discloses a method of manufacturing a cold rolled steel sheet of the aforementioned type which exhibits an excellent deep drawing property.
Unexamined Japanese Patent Publication No. 2-200730 (published August 9, 1990) discloses a method of manufacturing a cold rolled steel sheet of the aforementioned type which exhibits an excellent press formability. In any of these methods, although B is added to improve the resistance to cold-work embrittlement, there is no concrete disclosure to exhibit brittle transition temperature. Also, coiling is performed at a high temperature of 640~C or above which impairs descaling ability in a pickling process.
Therefore, in any of these methods, a sufficient improvement in the resistance of cold-work embrittlement cannot be expected.
Unexamined Japanese Patent Publication No.
63-241122 ~published October 6, 1988) discloses a method of manufacturing a continuously galvanized steel sheet for use in a super deep drawing. In this method, the proportion of B
contained is 0.0010 % or below, which is too small to improve ~A 7 2081 4~6 the resistance to cold-work embrittlement.
Unexamined Japanese Patent Publication No. 62-40318 (published February 21, 1987) discloses a method of manufacturing a cold rolled steel sheet exhibiting an excellent deep drawing property. Unexamined Japanese Patent Publication No. 1-188630 (published July 27, 1989) discloses a method of manufacturing a cold rolled steel sheet exhibiting an excellent press formability. However, in any of these methods, there is no concrete description of the resistance to cold-work embrittlement, and annealing is conducted at a temperature ranging between the recrystallization temperature and 800C. Therefore, a sufficient improvement of the resistance to cold-work embrittlement cannot be expected.
Unexamined Japanese Patent Publication No.
61-133323 (published June 20, 1986) discloses a method of manufacturing a steel sheet exhibiting an excellent formability. Unexamined Japanese Patent Publication No.
62-205231 (published September 9, 1987) discloses a method of manufacturing a high-strength steel sheet. Both of these methods are disclosed to the manufacture of a slab thinner than a normal one and to alleviation or simplification of the rolling process of steel sheet using such a thin slab.
However, in the former method, there is no concrete description on the conditions of the annealing which is conducted subsequent to the cold rolling process. Although there is a concrete disclosure of the resistance to cold-work embrittlement, the effect thereof is insufficient. In the .;~ ~ 73461-39 i A
latter method, there is a concrete disclosure of the annealing which is conducted at a temperature of 775~C or below. However, sufficient improvement in the resistance to cold-work embrittlement cannot to be expected under such conditions.
In any of the aforementioned conventional methods, it is thus difficult to readily obtain a cold rolled steel sheet exhibiting an excellent deep drawing property and an excellent resistance to cold-work embrittlement.
Planar anisotropy, known as one of barometers of the press formability, is generally evaluated by ~r. The closer to zero the planar anisotropy value is, the more uniform characteristics in each direction can be obtained, which is desirable in terms of press formability. Unexamined Japanese Patent Publication No. 61-64852 (published April 3, 1986) discloses a method of improving this planar anisotropy by adding a relatively large amount of Nb in an extra low carbon steel. Although this method is effective in improving the planar anisotropy, it deteriorates elongation (El) or r value. No method of improving the resistance to cold-work embrittlement as well as the planar anisotropy has been disclosed.
SUMMARY OF THE INVENTION
It is an object of the present invention to provide a method of manufacturing a cold rolled steel sheet for use in deep drawing which exhibits an excellent resistance to cold-work embrittlement and a small planar anisotropy while maintaining an excellent deep drawing property without the need for finely controlling the manufacturing conditions even when a continuous annealing process is employed.
The present inventors have made intensive studies on the composition to be added and the manufacturing method and discovered that it is possible to manufacture a cold rolled steel sheet for use in deep drawing which exhibits an excellent resistance to cold-work embrittlement and a slnall planar anisotropy from an extra low carbon steel in which Ti, Nb, B and Al are present each in an adequate amount by adequately setting the hot rolling and annealing conditions in the manufacturing process.
That is, the present invention provides a method of manufacturing a cold rolled steel sheet which exhibits an excellent resistance to cold-work embrittlement and a small planar anisotropy which comprises the steps of preparing, as a material, a steel whose composition consists of:
C : 0.004 wt% or less 2~81~96 Si : 0.10 wt% or less Mn : 0.50 wt% or less Ti : between 0.01 wt% and 0.10 wt%
Nb : between 0.003 wt% and 0.03 wt%
B : between 0.001 wt% and 0.004 wt%
Al : between 0.03 wt% and 0.10 wt%
P : 0.025 wt% or less S : 0.01 wt% or less N : 0.006 wt% or less Ti and C satisfying the following equation:
BACKGROUND OF THE INVENTION
Field of the Invention The present invention relates to a method of manufacturing a cold rolled steel sheet that exhibits excellent resistance to cold-work embrittlement and a small planar anisotropy by the continuous annealing method which is suitable as a pressed steel sheet for use in automobiles.
Description of the Related Art When a cold rolled steel sheet is manufactured, a continuous annealing, including heating and cooling which last for a short period of time, is generally conducted subsequent to the cold rolling. In this continuous annealing process, the material quality of the product is greatly affected by the chemical composition of the material. Hence, to obtain a steel sheet exhibiting excellent deep drawing property and stretchability, it has been the practice to add a carbide/nitride producing component, such as Ti or Nb, to the extra low carbon steel.
However, the steel sheet in which Ti or Nb is present is characterized in that Ti is readily combined with C, S, N or O in the steel to form a precipitate.
Consequently, the grain boundary is cleaned and the grain boundary strength is thus greatly reduced, increasing the 2~81496 possibility that a brittle fracture (the fracture due to cold-work embrittlement) will occur after deep drawing.
Also, it has been a practice to obtain a high-strength steel sheet by adding Mn, Si or P to the steel material.
In that case, however, since Si and P readily embrittle the steel sheet, the resistance to cold-work embrittlement greatly deteriorates. To improve such a drawback, B has been added to the steel in the form of a solid solution to increase the grain boundary strength, like C.
However, it is well known that adding B deteriorates the formability. Therefore, the proportion of B to be added is restricted to such a small value that sufficient resistance to cold-work embrittlement cannot be obtained.
Various other methods of improving the deep drawing property and stretchability of the steel sheet by controlling the conditions of hot rolling, cold rolling or annealing during the manufacturing process of the steel sheet have also been suggested. Generally, the hot rolling finishing temperature is set to an Ar3 transformation point or above from the viewpoint of improving the deep drawing property. The coiling temperature is between 650 and 800C from the viewpoint of improving the formability, especially deep drawing properties. The annealing temperature is set to a 208 ~ 496 relatively low temperature which is equal to or higher than the recrystallization temperature and which is effective in terms of the energy.
Unexamined Japanese Patent Publication No.
62-278232 (published December 3, 1987) discloses a method of manufacturing a cold rolled steel sheet of the aforementioned type for use in non-aging deep drawing by the direct hot-rolling method. Unexamined Japanese Patent Publication No.
1-177321 (published July 13, 1989) discloses a method of manufacturing a cold rolled steel sheet of the aforementioned type which exhibits an excellent deep drawing property.
Unexamined Japanese Patent Publication No. 2-200730 (published August 9, 1990) discloses a method of manufacturing a cold rolled steel sheet of the aforementioned type which exhibits an excellent press formability. In any of these methods, although B is added to improve the resistance to cold-work embrittlement, there is no concrete disclosure to exhibit brittle transition temperature. Also, coiling is performed at a high temperature of 640~C or above which impairs descaling ability in a pickling process.
Therefore, in any of these methods, a sufficient improvement in the resistance of cold-work embrittlement cannot be expected.
Unexamined Japanese Patent Publication No.
63-241122 ~published October 6, 1988) discloses a method of manufacturing a continuously galvanized steel sheet for use in a super deep drawing. In this method, the proportion of B
contained is 0.0010 % or below, which is too small to improve ~A 7 2081 4~6 the resistance to cold-work embrittlement.
Unexamined Japanese Patent Publication No. 62-40318 (published February 21, 1987) discloses a method of manufacturing a cold rolled steel sheet exhibiting an excellent deep drawing property. Unexamined Japanese Patent Publication No. 1-188630 (published July 27, 1989) discloses a method of manufacturing a cold rolled steel sheet exhibiting an excellent press formability. However, in any of these methods, there is no concrete description of the resistance to cold-work embrittlement, and annealing is conducted at a temperature ranging between the recrystallization temperature and 800C. Therefore, a sufficient improvement of the resistance to cold-work embrittlement cannot be expected.
Unexamined Japanese Patent Publication No.
61-133323 (published June 20, 1986) discloses a method of manufacturing a steel sheet exhibiting an excellent formability. Unexamined Japanese Patent Publication No.
62-205231 (published September 9, 1987) discloses a method of manufacturing a high-strength steel sheet. Both of these methods are disclosed to the manufacture of a slab thinner than a normal one and to alleviation or simplification of the rolling process of steel sheet using such a thin slab.
However, in the former method, there is no concrete description on the conditions of the annealing which is conducted subsequent to the cold rolling process. Although there is a concrete disclosure of the resistance to cold-work embrittlement, the effect thereof is insufficient. In the .;~ ~ 73461-39 i A
latter method, there is a concrete disclosure of the annealing which is conducted at a temperature of 775~C or below. However, sufficient improvement in the resistance to cold-work embrittlement cannot to be expected under such conditions.
In any of the aforementioned conventional methods, it is thus difficult to readily obtain a cold rolled steel sheet exhibiting an excellent deep drawing property and an excellent resistance to cold-work embrittlement.
Planar anisotropy, known as one of barometers of the press formability, is generally evaluated by ~r. The closer to zero the planar anisotropy value is, the more uniform characteristics in each direction can be obtained, which is desirable in terms of press formability. Unexamined Japanese Patent Publication No. 61-64852 (published April 3, 1986) discloses a method of improving this planar anisotropy by adding a relatively large amount of Nb in an extra low carbon steel. Although this method is effective in improving the planar anisotropy, it deteriorates elongation (El) or r value. No method of improving the resistance to cold-work embrittlement as well as the planar anisotropy has been disclosed.
SUMMARY OF THE INVENTION
It is an object of the present invention to provide a method of manufacturing a cold rolled steel sheet for use in deep drawing which exhibits an excellent resistance to cold-work embrittlement and a small planar anisotropy while maintaining an excellent deep drawing property without the need for finely controlling the manufacturing conditions even when a continuous annealing process is employed.
The present inventors have made intensive studies on the composition to be added and the manufacturing method and discovered that it is possible to manufacture a cold rolled steel sheet for use in deep drawing which exhibits an excellent resistance to cold-work embrittlement and a slnall planar anisotropy from an extra low carbon steel in which Ti, Nb, B and Al are present each in an adequate amount by adequately setting the hot rolling and annealing conditions in the manufacturing process.
That is, the present invention provides a method of manufacturing a cold rolled steel sheet which exhibits an excellent resistance to cold-work embrittlement and a small planar anisotropy which comprises the steps of preparing, as a material, a steel whose composition consists of:
C : 0.004 wt% or less 2~81~96 Si : 0.10 wt% or less Mn : 0.50 wt% or less Ti : between 0.01 wt% and 0.10 wt%
Nb : between 0.003 wt% and 0.03 wt%
B : between 0.001 wt% and 0.004 wt%
Al : between 0.03 wt% and 0.10 wt%
P : 0.025 wt% or less S : 0.01 wt% or less N : 0.006 wt% or less Ti and C satisfying the following equation:
3 ~ Ti*/C ~ 12 where Ti* = Ti - (48/14)N - (48/32)S
balance : iron and unavoidable impurities, performing a hot rolling on the material steel under the conditions of a finish temperature between 800C and 900C, coiling the material at a temperature lower than 650C, performing a cold rolling, performing a continuous annealing at a temperature between 830C and an Ac3 transformation point, and performing skin pass rolling.
Other features and variations of the present invention will be apparent from the following description taken in connection with the accompanying drawings.
BRIEF DESCRIPTION OF THE DRAWINGS
Fig. l(a) is a graph showing the relationship between the coiling temperature and the brittle transition temperature;
Fig. l(b) is a graph showing the coiling temperature and the planar anisotropy (~r);
Fig. 2(a) is a graph showing the relation between the annealing temperature and the brittle transition temperature;
Fig. 2(b) is a graph showing the relation between the annealing temperature and the planar anisotropy (~r);
and Fig. 3 is a graph showing the relation between the thickness of the steel and the brittle transition temperature regarding steels in which different amounts of B are present.
DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENT
The present invention will be described below concretely.
First, the reason for the restrictions placed on the compositions will be explained.
C : 0.004 wt% or less A smaller possible proportion of C is advantageous to improve the material quality. An increase in the amount of C contained increases the amount of Ti required to fix C, thus increasing the amount of precipitates produced and thereby deteriorating the material quality.
More than 0.004 wt% of C greatly deteriorates the material quality. Therefore, up to 0.004 wt% of C is preferred.
Si : 0.10 wt% or less Although the presence of Si is advantageous to obtain adequate steel strength, it promotes the cold-work embrittlement and degrades the phosphatability. Thus, the upper limit of the proportion of Si is set to 0.10 Wt%.
Mn : 0.50 wt% or less Although the inclusion of Mn is effective to obtain an adequate strength of the steel, as in the case of Si, it increases the tendency for a solid solution to be produced and hence deteriorates the drawing property.
The presence of Mn also increases the production cost.
Hence, the upper limit of the proportion of Mn is set to 0.50 wt%.
Ti : 0.01 to 0.1 wt%
3 ~ Ti*/C ~ 12 where Ti* = Ti - t48/14)N - (48/32)S
The presence of Ti promotes precipitation of N and S and hence improves the deep drawing property. That is, in a cold rolled steel sheet on which the continuous annealing has been conducted, a reduction in the amounts of C, N and S contained alone is not enough to provide the press formability which is as good as that of a steel sheet which has been subjected to the box annealing process. In this invention, Ti promotes precipitation of N and S in the hot rolling process. Precipitation of C
is promoted by a combination of Ti and Nb which will be described below. Precipitation of N by Ti enables B to be present in a solid solution which is effective to improve the resistance to cold-work embrittlement.
To stabilize C, N and S, at least 0.01 wt% of Ti must be added. More than 0.1 wt% of Ti does not increase the effect thereof.
Furthermore, it is necessary for Ti and C to be added in a range which satisfies the following equation (1) 3 S Ti*/C S 12 where Ti* = Ti - (48/14)N - (48/32)S.
The amount of Ti obtained by the above equation is the effective amount of Ti other than the amount which is consumed as nitride or sulfide. When Ti*/C < 3, if coiling is performed at a low temperature of 650C or less during the hot rolling process, as in the case of the present invention, part of C remains in the form of a solid solution, deteriorating the deep drawing property. When Ti*/C > 12, although the deep drawing property does not deteriorate, the phosphatability deteriorates. As a result, 3 S Ti*/C S 12.
2o8lq96 Nb : 0.003 to 0.03 wt%
The presence of Nb, which is a carbide forming component, improves the deep drawing property. The addition of Nb together with Ti increases the average r value and elongation. At least 0.003 wt% is required to obtain the effect of Nb. However, more than 0.03 wt% of Nb reduces the elongation. Thus, the desired proportion of Nb is between 0.003 wt% and 0.03 wt%.
B : 0.001 to 0.004 wt%
As mentioned above, the addition of B intensifies the grain boundary, like C, and hence improves the resistance to cold-work embrittlement. However, an excessive proportion of B increases the tendency for the average r value and elongation to deteriorate, and thus is not desirable in terms of the steel sheet for use in deep drawing. A preferred proportion of B is between 0.001 wt% and 0.004 wt%.
Al : 0.03 to 0.1 wt%
Al is a nitride forming component. The addition of Al together with Ti and Nb forms composite precipitates which are inferred as (Ti, Nb)C and (Ti, Al)N and hence promotes precipitation of C and N. It also improves the formability, particularly, the deep drawing property and reduces the planar anisotropy. At least 0.03 wt% of Al is necessary for the above-mentioned effects. More than 208 1 49~
0.1 wt% of Al does not improve the effect of Al and increases the production cost. Therefore, a desired proportion of Al is between 0.03 wt% and 0.1 wt%.
P : 0.025 wt% or less An excessive proportion of P increases the amount of grain boundary which is segregated and hence promotes the grain boundary embrittlement, and thus, deteriorates the resistance to cold-work embrittlement. Hence, the smaller the proportion of P, the better. 0.025 wt% or less of P is allowable.
S : 0.01 wt% or less An excessive proportion of S, which is a hazardous component, readily promotes the grain boundary embrittlement and thus deteriorates the resistance to cold-work embrittlement. Thus, a smaller possible proportion of S is desired. 0.01 wt% or less of S is allowable.
N : 0.006 wt% or less Like C, a smaller possible proportion of N is desirable from the viewpoint of improvement in the formability, particularly, deep drawing properties. The presence of N also deteriorates the resistance to strain aging. Thus, up to 0.006 wt% of N is allowable.
The reason for the restrictions placed on the manufacturing process conditions in the present invention will be described below. 2 08 1 4 9 6 Steel making process Steel may be manufactured in a normal method which employs, for example, a converter. There is no restriction on the conditions of the steel making process.
Steel may be manufactured in a normally employed continuous casting or ingot casting method.
Hot rolled process Finishing temperature : 800 to 900C
A finishing temperature lower than 800C
deteriorates the average r value and the elongation due to residual strain. A finishing temperature higher than 900C increases the size of the grains and hence deteriorates the average r value. Thus, a desired finishing temperature range is from 800C and 900C.
Coiling temperature : lower than 650C
Conventionally, a high coiling temperature ranging from 650C to 800C has been employed because it has been considered that coiling conducted at such a high temperature further increases the size of the TiC
precipitates and thus improves the elongation and average r value. It has also been considered that nuclei of TiC
and (Ti, Al)N are not readily generated and the precipitation speed is thus slowed down or precipitation is made incomplete in the coiling conducted at a low temperature, making precipitation of C and N insufficient and deteriorating the elongation ar-d average r value.
The present inventors made various experiments in which different coiling temperatures were employed, and discovered that coiling conducted at a low temperature provided a steel sheet which exhibited an excellent resistance to cold-work embrittlement and a small planar anisotropy.
The results of the experiments are shown in Fig. 1 (a) which is a graph showing the relation between the coiling temperature and the brittle transition temperature which is the index of the cold-work embrittlement. Fig. 1 (b) is a graph showing the relation between the coiling temperature and the planar anisotropy ~r. As shown in these figures, a reduction in the annealing temperature improves the resistance to cold-work embrittlement and reduces the planar anisotropy.
In the steel having the composition restricted by the present invention, it is considered that the planar anisotropy is reduced because precipitation of (Ti, Nb)C
and (Ti, ~l)N begins in the high-temperature range obtained before the hot rolling is finished and is promoted in the coiling conducted at a low temperature, i.e., from about 300C to lower than 650C, precipitating C and N to a sufficient extent and reducing the size of the grains which have been subjected to the hot rolling process. It is also considered that the formation of such precipitates promotes segregation of B
into the grain boundary, intensifies the grain boundary and thus improves the resistance to cold-work embrittlement.
Thus, the upper limit of the coiling temperature is set to 650C from the viewpoint of an improvement in the resistance to cold-work embrittlement and a reduction in the planar anisotropy. Although there is no restriction on the lower limit, a desirable lower limit is set to 300C with the cooling ability and cooling time or the coil shape obtained taken into consideration.
The samples used in the aforementioned experiments were manufactured under the following conditions using, as a material, a steel which contained 0.003 wt% of C, 0.01 wt% of Si, 0.15 wt% of Mn, 0.03 wt% of Ti, 0.005 wt%
of Nb, 0.002 wt% of B, 0.06 wt% of Al, 0.015 wt% of P, 0.005 wt% of S and 0.004 wt% of N.
Hot rolling finishing temperature : 890C
Coiling temperature : 300 to 850C
Cold rolling reduction : 80%
Thickness of a cold rolled sheet : 0.7 mm Continuous annealing conditions : 860C and 20 2o8l496 seconds Skin pass reduction : 1%
The brittle transition temperature was measured by measuring the highest temperature at which the brittle fracture occurred in each of the conical cup samples each having a blank diameter of 50 mm, a diameter of a dice of 24.4 mm and a punch diameter of 20.64 mm in the crash tests by employing different testing temperatures.
The planar anisotropy ~r was calculated by the following equation (2) using the value in the L direction (the direction of rolling) rL, the value in the D
direction (the direction which is 45 degrees from the direction of rolling) rD and the value in the C direction (the direction which is 90 degrees from the direction of rolling) rc which were measured using the sample to which a tensile strain of 15~ was applied beforehand:
~r = (rc + rL - 2rD)/2 ... (2) As is clear from Fig. 1 (b), a desirable range of the planar anisotropy ~r is as follows:
0 ~ ~r ' 0.25 A planar anisotropy ~r of more than 0.25 increases the inhomogeneous strain distribution and thus deteriorates the formability.
Continuous annealing temperature : 830C to Ac3 transformation point 2081 4q6 Conventionally, no restriction has been placed on the annealing temperature in the continuous annealing process because it has been considered that the material characteristics are determined by the hot rolling conditions. However, the present inventors have researched and found that the annealing temperature greatly affected cold-work embrittlement (the brittle transition temperature) and the planar anisotropy (~r), as shown in Figs. 2 (a) and 2 (b).
Fig. 2 (a) shows the relation between the annealing temperature and the brittle transition temperature. Fig.
2 (b) shows the relation between the annealing temperature and the planar anisotropy (~r).
It is considered that the resistance to cold-work embrittlement was not improved in the annealing conducted at a temperature less than 830C because segregation of B into the grain boundary was insufficient. It is also considered that the planar anisotropy was not reduced in the annealing conducted at a temperature less then 830C
because the recrystallized grain orientation was affected by the cold-rolled grain orientation.
In an annealing conducted at a temperature higher than the Ac3 transformation point, the size of the grains will increase, deteriorating the resistance to cold-work embrittlement and increasing the planar anisotropy due to the transformation.
Thus, a preferred continuous annealing temperature is from 830C and Ac3 transformation point from the viewpoint of improvement in the resistance to cold-work embrittlement and reduction in the planar anisotropy.
The samples employed in the experiments were manufactured under the following conditions using, as a material, a steel which contained 0.004 wt% of C, 0.02 wt% of Si, 0.19 wt% of Mn, 0.025 wt% of Ti, 0.01 wt% of Nb, 0.0025 wt% of B, 0.08 wt% of Al, 0.02 wt% of P, 0.006 wt% of S and 0.003 wt% of N.
Hot rolling finishing temperature : 880C
Coiling temperature : 600C
Cold rolling reduction : 70%
Thickness of the cold rolled sheet : 1.2 mm Continuous annealing conditions : 700 to 950C and 20 seconds Skin pass reduction : 1%
The brittle transition temperature and ~r were measured in the same manner as the aforementioned one.
As stated above, the resistance to cold-work embrittlement is greatly affected by the chemical composition of the material and the hot rolling and continuous annealing temperatures. This resistance to cold-work embrittlement is also affected by the thickness 208I ~96 of the steel sheet. In the case of the same material, the thicker the steel sheet, the higher the brittle transition temperature of the resistance to cold-work embrittlement (see Fig. 3).
The advantages of the present invention can be most readily obtained when the thickness is 1.0 mm or more at which deterioration in the resistance to cold-work embrittlement most readily occurs. The upper limit of the thickness is set to 5.0 mm because it is difficult to manufacture a cold rolled steel sheet having a thickness of more than 5.0 mm.
The samples employed in the experiments were manufactured under the following conditions using, as a material, a steel which contained 0.003 wt% of C, 0.01 wt% of Si, 0.15 wt% of Mn, 0.026 wt% of Ti, 0.008 wt% of Nb, 0.0026 wt% (26 ppm) or 0.0005 wt% (5 ppm) of B, 0.07 wi% of Al, 0.021 wt% of P, 0.005 wt% of S and 0.002 wt%
of N and which had a thickness ranging from 0.6 mm to 3.1 mm.
Hot rolling finishing temperature : 880C
Coiling temperature : 600C
Continuous annealing conditions : 840C and 40 seconds Cold rolling reduction : 65 to 73 %
(The brittle transition temperature was measured in 2081~96 the same manner as the aforementioned one.) Other conditions Although regarding the cold rolling and skin pass rolling processes, the normally employed conditions can be used, a preferred cold rolling reduction is between 50 and 95 % while a preferred skin pass rolling is between 0.5 and 2 %.
Examples Table 1 shows the chemical composition of each of the slabs manufactured by the continuous casting method from a molten steel manufactured by a normal manufacturing process. After hot rolling was performed on the steels having the compositions shown in Table l under the conditions shown in Table 2 to obtain hot rolled sheet coils having a thickness of 3.5 mm, cold rolling was performed to obtain cold rolled sheets having a thickness of 1.2 mm. Thereafter, continuous annealing was conducted at various temperatures shown in Table 2, and then skin pass rolling was performed at a reduction of l %.
Table 1 C~ENICAL COMPOSITION t~TZ) SYMBOL Ti*/C REMARKS
C SiMn TiNb BAl P S N
A 0.0025 0.01 0.170.028 0.0050.00150.0530.012 0.0050.0035 3.4 SUITABLE
EXAMPLE
B 0.0016 0.02 0.130.035 0.0040.00250.0710.011 0.0060.0021 11.8 C 0.0018 0.01 0.090.021 0.0090.00180.0580.009 0.0050.0022 3.7 D 0.0021 0.01 0.120.028 0.0050.00220.0650.009 0.0040.0018 7.5 E 0.0029 0.01 0.120.005 0.006 - 0.061 0.011 0.0060.0033 -5.2 COMPARATIVE
EXAMPLE
Y 0.0022 0.02 0.10 _ 0.0090.00270.0710.011 0.0060.0021 -7.4 G 0.0019 0.02 0.110.035 - 0.0005 0.053 0.012 0.0060.0025 9.2 ~ 0.0024 0.01 0.160.012 0.0050.00160.0570.013 0.0050.0019 0.5 Underlined figure is out of the range restricted by the present invention Table 2 N0. SYM30L OF STEEL MATERIAL CHARACTERISTICS HOT ROLLING CONDITIONS ANNEALING REMARRS
TEMPERATURE C
YS TS El AVERAGE ~r Tcr *1 FDT *2 CT *3 kgf/mm2kgf/=m2 Ir VALUE C C C
1 A 16.8 30.5 52 2.20.18 -160 880 540 850 SUITABLE
EXAMPLE
2 B 17.3 31.0 52 2.10.21 -150 890 580 850 3 C 15.2 29.8 53 2.40.25 -140 885 610 870 4 D 15.9 30.1 52 2.20.17 -155 890 510 880 A 16.2 29.9 53 2.30.75 -70 880 680 870 COMPARISON
EXAMPLE
6 B 18.3 32.3 48 1.70.69 -100 880 580 770 7 E 20.3 34.7 46 1.61.03 -55 885 540 860 8 F 19.6 33.5 47 1.70.85 -100 870 535 860 9 G 20.1 33.9 44 1.60.77 -75 870 520 865 E 18.9 33.0 48 1.80.58 -150 870 580 875 Underlined figure is out of the range restricted by this invention *1 Tcr: Brittle transition temperature *2 FDT: Final finishing temperature *3 CT : Coiling temperture ~;~, 2081~g6 The tensile characteristics, the average r value, the planar anisotropy (~r) and the cold-work embrittlement (brittle transition temperature) of the thus-obtained cold rolled steel sheets were examined.
The results of the examinations are shown in Fig. 2.
The tensile test was conducted in conformity with JIS No. 5. The average r value was calculated from rL, rD
and rc by the following equation.
Average r value = (rL + 2rD + rc)/4 ~r and the brittle transition temperature were obtained in the same manner as the aforementioned ones.
As is clear from Table 2, in the examples (sample Nos. 1 through 4) of the present invention, TS ~ 29.5 Kgf/mm , El 2 50% and the average r value ~ 2Ø Also, the brittle transition temperature < -140C and ~r ~
0.25, that is, substantially no cold-work brittle fracture occurred and the planar anisotropy was very less.
In the comparative examples (sample Nos. 5 through 6) manufactured from the material having the composition restricted by the present invention under the manufacturing conditions which were out of the range restricted by the present invention, the bri~tle transition temperature was high and the planar anisotropy ~r ' 0.69. In the comparative examples (sample Nos. 7 208l 496 through 10) manufactured from the material having the composition which was out of range restricted by the present invention under the manufacturing conditions restricted by the present invention, the brittle transition temperature ' -100C, and ~r ' 0.58.
Thus, the cold rolled steel sheets alone which satisfy both the composition and manufacturing conditions restricted by the present invention have excellent characteristics.
The present invention is directed to manufacture of a cold rolled steel sheet for use in deep drawing which exhibits an excellent resistance to cold-work embrittlement and a very small planar anisotropy using, as a material, an extra low carbon steel in which adequate amounts of Ti, Nb, B and Al are present under the appropriate hot rolling and continuous annealing conditions even when the continuous annealing process is used.
The cold rolled steel sheet obtained in this invention is suitable for use in, for example, automobiles, where excellent press formability is required.
balance : iron and unavoidable impurities, performing a hot rolling on the material steel under the conditions of a finish temperature between 800C and 900C, coiling the material at a temperature lower than 650C, performing a cold rolling, performing a continuous annealing at a temperature between 830C and an Ac3 transformation point, and performing skin pass rolling.
Other features and variations of the present invention will be apparent from the following description taken in connection with the accompanying drawings.
BRIEF DESCRIPTION OF THE DRAWINGS
Fig. l(a) is a graph showing the relationship between the coiling temperature and the brittle transition temperature;
Fig. l(b) is a graph showing the coiling temperature and the planar anisotropy (~r);
Fig. 2(a) is a graph showing the relation between the annealing temperature and the brittle transition temperature;
Fig. 2(b) is a graph showing the relation between the annealing temperature and the planar anisotropy (~r);
and Fig. 3 is a graph showing the relation between the thickness of the steel and the brittle transition temperature regarding steels in which different amounts of B are present.
DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENT
The present invention will be described below concretely.
First, the reason for the restrictions placed on the compositions will be explained.
C : 0.004 wt% or less A smaller possible proportion of C is advantageous to improve the material quality. An increase in the amount of C contained increases the amount of Ti required to fix C, thus increasing the amount of precipitates produced and thereby deteriorating the material quality.
More than 0.004 wt% of C greatly deteriorates the material quality. Therefore, up to 0.004 wt% of C is preferred.
Si : 0.10 wt% or less Although the presence of Si is advantageous to obtain adequate steel strength, it promotes the cold-work embrittlement and degrades the phosphatability. Thus, the upper limit of the proportion of Si is set to 0.10 Wt%.
Mn : 0.50 wt% or less Although the inclusion of Mn is effective to obtain an adequate strength of the steel, as in the case of Si, it increases the tendency for a solid solution to be produced and hence deteriorates the drawing property.
The presence of Mn also increases the production cost.
Hence, the upper limit of the proportion of Mn is set to 0.50 wt%.
Ti : 0.01 to 0.1 wt%
3 ~ Ti*/C ~ 12 where Ti* = Ti - t48/14)N - (48/32)S
The presence of Ti promotes precipitation of N and S and hence improves the deep drawing property. That is, in a cold rolled steel sheet on which the continuous annealing has been conducted, a reduction in the amounts of C, N and S contained alone is not enough to provide the press formability which is as good as that of a steel sheet which has been subjected to the box annealing process. In this invention, Ti promotes precipitation of N and S in the hot rolling process. Precipitation of C
is promoted by a combination of Ti and Nb which will be described below. Precipitation of N by Ti enables B to be present in a solid solution which is effective to improve the resistance to cold-work embrittlement.
To stabilize C, N and S, at least 0.01 wt% of Ti must be added. More than 0.1 wt% of Ti does not increase the effect thereof.
Furthermore, it is necessary for Ti and C to be added in a range which satisfies the following equation (1) 3 S Ti*/C S 12 where Ti* = Ti - (48/14)N - (48/32)S.
The amount of Ti obtained by the above equation is the effective amount of Ti other than the amount which is consumed as nitride or sulfide. When Ti*/C < 3, if coiling is performed at a low temperature of 650C or less during the hot rolling process, as in the case of the present invention, part of C remains in the form of a solid solution, deteriorating the deep drawing property. When Ti*/C > 12, although the deep drawing property does not deteriorate, the phosphatability deteriorates. As a result, 3 S Ti*/C S 12.
2o8lq96 Nb : 0.003 to 0.03 wt%
The presence of Nb, which is a carbide forming component, improves the deep drawing property. The addition of Nb together with Ti increases the average r value and elongation. At least 0.003 wt% is required to obtain the effect of Nb. However, more than 0.03 wt% of Nb reduces the elongation. Thus, the desired proportion of Nb is between 0.003 wt% and 0.03 wt%.
B : 0.001 to 0.004 wt%
As mentioned above, the addition of B intensifies the grain boundary, like C, and hence improves the resistance to cold-work embrittlement. However, an excessive proportion of B increases the tendency for the average r value and elongation to deteriorate, and thus is not desirable in terms of the steel sheet for use in deep drawing. A preferred proportion of B is between 0.001 wt% and 0.004 wt%.
Al : 0.03 to 0.1 wt%
Al is a nitride forming component. The addition of Al together with Ti and Nb forms composite precipitates which are inferred as (Ti, Nb)C and (Ti, Al)N and hence promotes precipitation of C and N. It also improves the formability, particularly, the deep drawing property and reduces the planar anisotropy. At least 0.03 wt% of Al is necessary for the above-mentioned effects. More than 208 1 49~
0.1 wt% of Al does not improve the effect of Al and increases the production cost. Therefore, a desired proportion of Al is between 0.03 wt% and 0.1 wt%.
P : 0.025 wt% or less An excessive proportion of P increases the amount of grain boundary which is segregated and hence promotes the grain boundary embrittlement, and thus, deteriorates the resistance to cold-work embrittlement. Hence, the smaller the proportion of P, the better. 0.025 wt% or less of P is allowable.
S : 0.01 wt% or less An excessive proportion of S, which is a hazardous component, readily promotes the grain boundary embrittlement and thus deteriorates the resistance to cold-work embrittlement. Thus, a smaller possible proportion of S is desired. 0.01 wt% or less of S is allowable.
N : 0.006 wt% or less Like C, a smaller possible proportion of N is desirable from the viewpoint of improvement in the formability, particularly, deep drawing properties. The presence of N also deteriorates the resistance to strain aging. Thus, up to 0.006 wt% of N is allowable.
The reason for the restrictions placed on the manufacturing process conditions in the present invention will be described below. 2 08 1 4 9 6 Steel making process Steel may be manufactured in a normal method which employs, for example, a converter. There is no restriction on the conditions of the steel making process.
Steel may be manufactured in a normally employed continuous casting or ingot casting method.
Hot rolled process Finishing temperature : 800 to 900C
A finishing temperature lower than 800C
deteriorates the average r value and the elongation due to residual strain. A finishing temperature higher than 900C increases the size of the grains and hence deteriorates the average r value. Thus, a desired finishing temperature range is from 800C and 900C.
Coiling temperature : lower than 650C
Conventionally, a high coiling temperature ranging from 650C to 800C has been employed because it has been considered that coiling conducted at such a high temperature further increases the size of the TiC
precipitates and thus improves the elongation and average r value. It has also been considered that nuclei of TiC
and (Ti, Al)N are not readily generated and the precipitation speed is thus slowed down or precipitation is made incomplete in the coiling conducted at a low temperature, making precipitation of C and N insufficient and deteriorating the elongation ar-d average r value.
The present inventors made various experiments in which different coiling temperatures were employed, and discovered that coiling conducted at a low temperature provided a steel sheet which exhibited an excellent resistance to cold-work embrittlement and a small planar anisotropy.
The results of the experiments are shown in Fig. 1 (a) which is a graph showing the relation between the coiling temperature and the brittle transition temperature which is the index of the cold-work embrittlement. Fig. 1 (b) is a graph showing the relation between the coiling temperature and the planar anisotropy ~r. As shown in these figures, a reduction in the annealing temperature improves the resistance to cold-work embrittlement and reduces the planar anisotropy.
In the steel having the composition restricted by the present invention, it is considered that the planar anisotropy is reduced because precipitation of (Ti, Nb)C
and (Ti, ~l)N begins in the high-temperature range obtained before the hot rolling is finished and is promoted in the coiling conducted at a low temperature, i.e., from about 300C to lower than 650C, precipitating C and N to a sufficient extent and reducing the size of the grains which have been subjected to the hot rolling process. It is also considered that the formation of such precipitates promotes segregation of B
into the grain boundary, intensifies the grain boundary and thus improves the resistance to cold-work embrittlement.
Thus, the upper limit of the coiling temperature is set to 650C from the viewpoint of an improvement in the resistance to cold-work embrittlement and a reduction in the planar anisotropy. Although there is no restriction on the lower limit, a desirable lower limit is set to 300C with the cooling ability and cooling time or the coil shape obtained taken into consideration.
The samples used in the aforementioned experiments were manufactured under the following conditions using, as a material, a steel which contained 0.003 wt% of C, 0.01 wt% of Si, 0.15 wt% of Mn, 0.03 wt% of Ti, 0.005 wt%
of Nb, 0.002 wt% of B, 0.06 wt% of Al, 0.015 wt% of P, 0.005 wt% of S and 0.004 wt% of N.
Hot rolling finishing temperature : 890C
Coiling temperature : 300 to 850C
Cold rolling reduction : 80%
Thickness of a cold rolled sheet : 0.7 mm Continuous annealing conditions : 860C and 20 2o8l496 seconds Skin pass reduction : 1%
The brittle transition temperature was measured by measuring the highest temperature at which the brittle fracture occurred in each of the conical cup samples each having a blank diameter of 50 mm, a diameter of a dice of 24.4 mm and a punch diameter of 20.64 mm in the crash tests by employing different testing temperatures.
The planar anisotropy ~r was calculated by the following equation (2) using the value in the L direction (the direction of rolling) rL, the value in the D
direction (the direction which is 45 degrees from the direction of rolling) rD and the value in the C direction (the direction which is 90 degrees from the direction of rolling) rc which were measured using the sample to which a tensile strain of 15~ was applied beforehand:
~r = (rc + rL - 2rD)/2 ... (2) As is clear from Fig. 1 (b), a desirable range of the planar anisotropy ~r is as follows:
0 ~ ~r ' 0.25 A planar anisotropy ~r of more than 0.25 increases the inhomogeneous strain distribution and thus deteriorates the formability.
Continuous annealing temperature : 830C to Ac3 transformation point 2081 4q6 Conventionally, no restriction has been placed on the annealing temperature in the continuous annealing process because it has been considered that the material characteristics are determined by the hot rolling conditions. However, the present inventors have researched and found that the annealing temperature greatly affected cold-work embrittlement (the brittle transition temperature) and the planar anisotropy (~r), as shown in Figs. 2 (a) and 2 (b).
Fig. 2 (a) shows the relation between the annealing temperature and the brittle transition temperature. Fig.
2 (b) shows the relation between the annealing temperature and the planar anisotropy (~r).
It is considered that the resistance to cold-work embrittlement was not improved in the annealing conducted at a temperature less than 830C because segregation of B into the grain boundary was insufficient. It is also considered that the planar anisotropy was not reduced in the annealing conducted at a temperature less then 830C
because the recrystallized grain orientation was affected by the cold-rolled grain orientation.
In an annealing conducted at a temperature higher than the Ac3 transformation point, the size of the grains will increase, deteriorating the resistance to cold-work embrittlement and increasing the planar anisotropy due to the transformation.
Thus, a preferred continuous annealing temperature is from 830C and Ac3 transformation point from the viewpoint of improvement in the resistance to cold-work embrittlement and reduction in the planar anisotropy.
The samples employed in the experiments were manufactured under the following conditions using, as a material, a steel which contained 0.004 wt% of C, 0.02 wt% of Si, 0.19 wt% of Mn, 0.025 wt% of Ti, 0.01 wt% of Nb, 0.0025 wt% of B, 0.08 wt% of Al, 0.02 wt% of P, 0.006 wt% of S and 0.003 wt% of N.
Hot rolling finishing temperature : 880C
Coiling temperature : 600C
Cold rolling reduction : 70%
Thickness of the cold rolled sheet : 1.2 mm Continuous annealing conditions : 700 to 950C and 20 seconds Skin pass reduction : 1%
The brittle transition temperature and ~r were measured in the same manner as the aforementioned one.
As stated above, the resistance to cold-work embrittlement is greatly affected by the chemical composition of the material and the hot rolling and continuous annealing temperatures. This resistance to cold-work embrittlement is also affected by the thickness 208I ~96 of the steel sheet. In the case of the same material, the thicker the steel sheet, the higher the brittle transition temperature of the resistance to cold-work embrittlement (see Fig. 3).
The advantages of the present invention can be most readily obtained when the thickness is 1.0 mm or more at which deterioration in the resistance to cold-work embrittlement most readily occurs. The upper limit of the thickness is set to 5.0 mm because it is difficult to manufacture a cold rolled steel sheet having a thickness of more than 5.0 mm.
The samples employed in the experiments were manufactured under the following conditions using, as a material, a steel which contained 0.003 wt% of C, 0.01 wt% of Si, 0.15 wt% of Mn, 0.026 wt% of Ti, 0.008 wt% of Nb, 0.0026 wt% (26 ppm) or 0.0005 wt% (5 ppm) of B, 0.07 wi% of Al, 0.021 wt% of P, 0.005 wt% of S and 0.002 wt%
of N and which had a thickness ranging from 0.6 mm to 3.1 mm.
Hot rolling finishing temperature : 880C
Coiling temperature : 600C
Continuous annealing conditions : 840C and 40 seconds Cold rolling reduction : 65 to 73 %
(The brittle transition temperature was measured in 2081~96 the same manner as the aforementioned one.) Other conditions Although regarding the cold rolling and skin pass rolling processes, the normally employed conditions can be used, a preferred cold rolling reduction is between 50 and 95 % while a preferred skin pass rolling is between 0.5 and 2 %.
Examples Table 1 shows the chemical composition of each of the slabs manufactured by the continuous casting method from a molten steel manufactured by a normal manufacturing process. After hot rolling was performed on the steels having the compositions shown in Table l under the conditions shown in Table 2 to obtain hot rolled sheet coils having a thickness of 3.5 mm, cold rolling was performed to obtain cold rolled sheets having a thickness of 1.2 mm. Thereafter, continuous annealing was conducted at various temperatures shown in Table 2, and then skin pass rolling was performed at a reduction of l %.
Table 1 C~ENICAL COMPOSITION t~TZ) SYMBOL Ti*/C REMARKS
C SiMn TiNb BAl P S N
A 0.0025 0.01 0.170.028 0.0050.00150.0530.012 0.0050.0035 3.4 SUITABLE
EXAMPLE
B 0.0016 0.02 0.130.035 0.0040.00250.0710.011 0.0060.0021 11.8 C 0.0018 0.01 0.090.021 0.0090.00180.0580.009 0.0050.0022 3.7 D 0.0021 0.01 0.120.028 0.0050.00220.0650.009 0.0040.0018 7.5 E 0.0029 0.01 0.120.005 0.006 - 0.061 0.011 0.0060.0033 -5.2 COMPARATIVE
EXAMPLE
Y 0.0022 0.02 0.10 _ 0.0090.00270.0710.011 0.0060.0021 -7.4 G 0.0019 0.02 0.110.035 - 0.0005 0.053 0.012 0.0060.0025 9.2 ~ 0.0024 0.01 0.160.012 0.0050.00160.0570.013 0.0050.0019 0.5 Underlined figure is out of the range restricted by the present invention Table 2 N0. SYM30L OF STEEL MATERIAL CHARACTERISTICS HOT ROLLING CONDITIONS ANNEALING REMARRS
TEMPERATURE C
YS TS El AVERAGE ~r Tcr *1 FDT *2 CT *3 kgf/mm2kgf/=m2 Ir VALUE C C C
1 A 16.8 30.5 52 2.20.18 -160 880 540 850 SUITABLE
EXAMPLE
2 B 17.3 31.0 52 2.10.21 -150 890 580 850 3 C 15.2 29.8 53 2.40.25 -140 885 610 870 4 D 15.9 30.1 52 2.20.17 -155 890 510 880 A 16.2 29.9 53 2.30.75 -70 880 680 870 COMPARISON
EXAMPLE
6 B 18.3 32.3 48 1.70.69 -100 880 580 770 7 E 20.3 34.7 46 1.61.03 -55 885 540 860 8 F 19.6 33.5 47 1.70.85 -100 870 535 860 9 G 20.1 33.9 44 1.60.77 -75 870 520 865 E 18.9 33.0 48 1.80.58 -150 870 580 875 Underlined figure is out of the range restricted by this invention *1 Tcr: Brittle transition temperature *2 FDT: Final finishing temperature *3 CT : Coiling temperture ~;~, 2081~g6 The tensile characteristics, the average r value, the planar anisotropy (~r) and the cold-work embrittlement (brittle transition temperature) of the thus-obtained cold rolled steel sheets were examined.
The results of the examinations are shown in Fig. 2.
The tensile test was conducted in conformity with JIS No. 5. The average r value was calculated from rL, rD
and rc by the following equation.
Average r value = (rL + 2rD + rc)/4 ~r and the brittle transition temperature were obtained in the same manner as the aforementioned ones.
As is clear from Table 2, in the examples (sample Nos. 1 through 4) of the present invention, TS ~ 29.5 Kgf/mm , El 2 50% and the average r value ~ 2Ø Also, the brittle transition temperature < -140C and ~r ~
0.25, that is, substantially no cold-work brittle fracture occurred and the planar anisotropy was very less.
In the comparative examples (sample Nos. 5 through 6) manufactured from the material having the composition restricted by the present invention under the manufacturing conditions which were out of the range restricted by the present invention, the bri~tle transition temperature was high and the planar anisotropy ~r ' 0.69. In the comparative examples (sample Nos. 7 208l 496 through 10) manufactured from the material having the composition which was out of range restricted by the present invention under the manufacturing conditions restricted by the present invention, the brittle transition temperature ' -100C, and ~r ' 0.58.
Thus, the cold rolled steel sheets alone which satisfy both the composition and manufacturing conditions restricted by the present invention have excellent characteristics.
The present invention is directed to manufacture of a cold rolled steel sheet for use in deep drawing which exhibits an excellent resistance to cold-work embrittlement and a very small planar anisotropy using, as a material, an extra low carbon steel in which adequate amounts of Ti, Nb, B and Al are present under the appropriate hot rolling and continuous annealing conditions even when the continuous annealing process is used.
The cold rolled steel sheet obtained in this invention is suitable for use in, for example, automobiles, where excellent press formability is required.
Claims (4)
1. A method of manufacturing a cold rolled steel sheet exhibiting an excellent resistance to cold-work embrittlement and a small planar anisotropy, comprising the steps of:
preparing, as a material, a steel whose composition consists of:
C : 0.004 wt% or less Si : 0.10 wt% or less Mn : 0.50 wt% or less Ti : between 0.01 wt% and 0.10 wt%
Nb : between 0.003 wt% and 0.03 wt%
B : between 0.001 wt% and 0.004 wt%
Al : between 0.03 wt% and 0.10 wt%
P : 0.025 wt% or less S : 0.01 wt% or less N : 0.006 wt% or less Ti and C satisfying the following equation:
3 ? Ti*/C ? 12 where Ti* = Ti - (48/14)N - (48/32)S
balance : iron and unavoidable impurities;
performing a hot rolling on the material steel under the conditions of a finishing temperature between 800°C
and 900°C;
coiling the material at a temperature lower than 650°C;
performing a cold rolling;
performing a continuous annealing at a temperature between 830°C and Ac3 transformation point; and performing a skin pass rolling, wherein the small planar anisotropy (.DELTA.r) satisfies the following equation:
0 ?c .DELTA.r ? 0.25 where .DELTA.r = (rC + rL - 2rD)/2, rL : Lankford value in the direction of rolling, rD : Lankford value in the direction which is 45 degrees with respect to the direction of rolling, and rC : Lankford value in the direction which is 90 degrees with respect to the direction of rolling.
preparing, as a material, a steel whose composition consists of:
C : 0.004 wt% or less Si : 0.10 wt% or less Mn : 0.50 wt% or less Ti : between 0.01 wt% and 0.10 wt%
Nb : between 0.003 wt% and 0.03 wt%
B : between 0.001 wt% and 0.004 wt%
Al : between 0.03 wt% and 0.10 wt%
P : 0.025 wt% or less S : 0.01 wt% or less N : 0.006 wt% or less Ti and C satisfying the following equation:
3 ? Ti*/C ? 12 where Ti* = Ti - (48/14)N - (48/32)S
balance : iron and unavoidable impurities;
performing a hot rolling on the material steel under the conditions of a finishing temperature between 800°C
and 900°C;
coiling the material at a temperature lower than 650°C;
performing a cold rolling;
performing a continuous annealing at a temperature between 830°C and Ac3 transformation point; and performing a skin pass rolling, wherein the small planar anisotropy (.DELTA.r) satisfies the following equation:
0 ?c .DELTA.r ? 0.25 where .DELTA.r = (rC + rL - 2rD)/2, rL : Lankford value in the direction of rolling, rD : Lankford value in the direction which is 45 degrees with respect to the direction of rolling, and rC : Lankford value in the direction which is 90 degrees with respect to the direction of rolling.
2. A method according to claim 1, wherein the steel sheet has a thickness ranging from 1.0 mm and 5.0 mm.
3. A method according to claim 1 or 2, wherein the coiling is performed at a temperature in the range from 300°C
to lower than 650°C.
to lower than 650°C.
4. A method according to claim 3, wherein the coiling is performed at a temperature of from 300 to 600°C.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP282978/1991 | 1991-10-29 | ||
| JP3282978A JP2781297B2 (en) | 1991-10-29 | 1991-10-29 | Method for producing cold rolled thin steel sheet with excellent secondary work brittleness and low in-plane anisotropy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CA2081496A1 CA2081496A1 (en) | 1993-04-30 |
| CA2081496C true CA2081496C (en) | 1997-05-13 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA 2081496 Expired - Lifetime CA2081496C (en) | 1991-10-29 | 1992-10-27 | Method of manufacturing a cold rolled steel sheet exhibiting an excellent resistance to cold-work embrittlement and a small planar anisotropy |
Country Status (5)
| Country | Link |
|---|---|
| EP (1) | EP0539962B1 (en) |
| JP (1) | JP2781297B2 (en) |
| KR (1) | KR950013192B1 (en) |
| CA (1) | CA2081496C (en) |
| DE (1) | DE69225294T2 (en) |
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| JP3783439B2 (en) * | 1998-12-25 | 2006-06-07 | Ｊｆｅスチール株式会社 | Method for temper rolling of steel sheet |
| KR100504369B1 (en) * | 2000-12-22 | 2005-07-28 | 주식회사 포스코 | Low carbon cold rolled steel sheets and its manufacturing method having low plastic deformation and anisotropy index |
| KR100530077B1 (en) * | 2001-12-21 | 2005-11-22 | 주식회사 포스코 | Deep Drawing High Strength Steel Sheet With Secondary Working Brittleness Resistance and Formability and A Method for Manufacturing Thereof |
| KR100544724B1 (en) * | 2001-12-26 | 2006-01-24 | 주식회사 포스코 | Cold Rolled Steel Sheet with Superior Workability and Method for Manufacturing the Sheet |
| KR100957999B1 (en) * | 2002-12-09 | 2010-05-17 | 주식회사 포스코 | Method for manufacturing of cold rolled steel sheet having excellent workability |
| KR100685030B1 (en) * | 2005-07-08 | 2007-02-20 | 주식회사 포스코 | Steel sheet for deep drawing having excellent resistance to secondary work embrittlement, fatigue property and coatability, and method for manufacturing the same |
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| US4504326A (en) * | 1982-10-08 | 1985-03-12 | Nippon Steel Corporation | Method for the production of cold rolled steel sheet having super deep drawability |
| JPS61276927A (en) * | 1985-05-31 | 1986-12-06 | Kawasaki Steel Corp | Production of cold rolled steel sheet having good deep drawability |
| US4889566A (en) * | 1987-06-18 | 1989-12-26 | Kawasaki Steel Corporation | Method for producing cold rolled steel sheets having improved spot weldability |
| EP0421087B1 (en) * | 1989-08-09 | 1994-11-30 | KABUSHIKI KAISHA KOBE SEIKO SHO also known as Kobe Steel Ltd. | Method of manufacturing a steel sheet |
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- 1991-10-29 JP JP3282978A patent/JP2781297B2/en not_active Expired - Fee Related
-
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- 1992-10-27 CA CA 2081496 patent/CA2081496C/en not_active Expired - Lifetime
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- 1992-10-28 DE DE1992625294 patent/DE69225294T2/en not_active Revoked
Also Published As
| Publication number | Publication date |
|---|---|
| JPH05117758A (en) | 1993-05-14 |
| JP2781297B2 (en) | 1998-07-30 |
| KR950013192B1 (en) | 1995-10-25 |
| EP0539962B1 (en) | 1998-04-29 |
| DE69225294T2 (en) | 1998-08-20 |
| EP0539962A1 (en) | 1993-05-05 |
| CA2081496A1 (en) | 1993-04-30 |
| DE69225294D1 (en) | 1998-06-04 |
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| Date | Code | Title | Description |
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| EEER | Examination request | ||
| MKEX | Expiry |