Cold rolled steel having excellent machinability and production thereof

Description

TECHNICAL FIELD
This invention is directed to remelting of scrap material by an electric furnace, etc., for re-utilizing scrap steel which has been remarkably increasing in recent years from automobile scrap, and so forth. More particularly, the present invention relates to a cold rolled steel sheet having excellent cold formability, though it has a high N content, and to a production method of such a cold rolled steel sheet.
BACKGROUND ART
Recently, quality of a cold rolled steel sheet for forming and its production technologies have made remarkable progress, and particularly, a Rankford value (hereinafter referred to as the "r value") representing deep drawability when cold has become as high as 1.7 or more.
As a technology for obtaining such high performance, Japanese Examined Patent Publication (Kokoku) No. 44-18066 discloses a technology which fixes and stabilizes C by adding 0.02 to 0.5% of Ti to a steel containing 0.001 to 0.02% of C and not greater than 0.015% of 0.
Japanese Examined Patent Publication (Kokoku) No. 3-54186 discloses a method which reduces both C and N contents to at most 0.005% and adds Ti and Nb, and Japanese Examined Patent Publication (Kokoku) No. 53-12899 discloses a technology which minimizes the C and N contents and adds Ti, Nb and B for fixing them.
These prior art technologies are based on the common technical concept of reducing the C and N contents as much as possible and obtain a cold rolled steel sheet having excellent non-ageability and excellent cold formability.
Re-utilization of steel scrap which is generated in large quantities everywhere has become a very important problem at present. To re-utilize the scrap, it is common to arc melt the scrap by an electric furnace, or the like. In this case, the N content in the steel reaches a high level of 60 ppm or more because N.sub.2 in the air comes into the steel.
When the N content is great, formability drops remarkably. Particularly in a high nitrogen region having an N content of 60 ppm or more, forming involving large deformation such as deep drawing becomes hardly possible. Means such as vacuum degassing must be employed in order to reduce this nitrogen content, and the production cost unavoidably increases.
Japanese Unexamined Patent Publication (Kokai) No. 57-26124 can be cited as a prior art reference which discloses a production technology of a cold rolled steel sheet having a high N content. This technology continuously anneals a cold rolled steel sheet having a specific C, Mn and Al content and containing 30 to 200 ppm of N at a predetermined temperature, and obtains a cold rolled steel sheet having excellent bake-hardenability. Because this cold rolled steel sheet contains a large quantity of N, a content of free N (the balance obtained by subtracting N bonded to Ti, Nb, etc., from the total N content) can be secured. This free N exhibits bake-hardenability. This reference discloses also that when this steel sheet is allowed to contain P, Si and Ti, its strength can also be improved. Nonetheless, Japanese Unexamined Patent Publication (Kokai) No. 57-26124 does not at all disclose a technology for securing formability of a high N steel.
As means for solving this problem, the inventors of the present invention invented, and filed a patent application for, a high N content hot rolled steel sheet having high strength and high formability and a production technology thereof in Japanese Patent Application No. 4-292352. This reference allows a high N (50 to 150 ppm) steel to contain C so that the carbon equivalent becomes 0.1 to 0.45%, secures an area fraction of pearlite of at least 5% so as to secure uniform elongation after cold forming, and disperses TiN of which sizes 1 .mu.m or more in a weight proportion of 0.0008 to 0.015% so as to obtain a hot rolled steel sheet having a tensile strength of 34 kgf/mm.sup.2 or more.
However, this reference does not at all suggest formability of a high N cold rolled steel sheet.
When re-utilizing a scrap and using an electric furnace for this re-utilization, the present invention provides a cold rolled steel sheet having excellent formability, though it has a high N content, and a production method which does not require processing such as vacuum degassing.
CONSTITUTION OF INVENTION
The inventors of the present invention have examined the components of a steel, its crystal structure, the forms of precipitates (kind, amount, distribution condition) and mechanical properties of the steel sheet after cold rolling and annealing.
First of all, the experimental results which have resulted in completion of the present invention will be explained.
An Al killed steel was produced by using an electric furnace. Because it was possible to predict in advance that the N content became high, Ti was added so as to fix N and to make it harmless. Steel components in the ladle were 302 ppm of C, 0.009% of Si, 0.163% of Mn, 0.005% of P, 0.0118% of S, 0.0319% of Al, 122 ppm of N, 0.029% of Ti (free N of 37 ppm when Ti is added), 0.015% of Cr, 0.016% of Cu and 0.026% of Ni.
This steel was cast and hot rolled, cold rolled and annealed under various conditions, then various properties thereof (yield point, tensile strength, elongation, r value) were examined.
More concretely, a wide variety of properties could be obtained such as a steel sheet having good formability with a yield point of 16 to 18 kgf/mm.sup.2, a tensile strength of 30 to 32 kgf/mm.sup.2, elongation of 44 to 46% and an r value of 1.7 to 1.8 or a steel sheet having very poor formability with a yield point of 18 to 25 kgf/mm.sup.2, a tensile strength of 37 to 39 kgf/mm.sup.2, elongation of 36 to 38% and an r value of 1.4 to 1.5.
On the assumption that variance of these properties was primarily associated with the quantities of the precipitates consisting principally of TiN and their forms (size, dispersion state), the inventors of this invention changed the cooling rate (to various values between 10.degree. C./min and 82.degree. C./min) at the time of casting and examined the relation between the mechanical properties of the steel sheet after annealing and the quantity and form of TiN. In addition, a material having the same components but having a low N content of 26 ppm (hereinafter called the "corresponding material") was treated by the same process, and similar examinations were carried out.
Incidentally, the heating temperature of the slab was 1,200.degree. C., the hot rolling temperature was 880.degree. C., the thickness of the hot rolled sheet was 3.5 mm, the thickness of the cold rolled sheet was 0.8 mm (reduction ratio: 88%) and the continuous annealing condition was at 820.degree. C. for one minute.
Inspection of dozens of fields per sample was carried out for inclusions such as TiN, etc., by using an electronmicroscope, and the size distribution of TiN and the weight distribution on the basis of the former were determined. FIGS. 1(A), 1(B), 1(C) and 1(D) show the relation between the cooling rate at the time of casting and the form of TiN (abscissa) and the resulting material properties (ordinate).
Since the shape of the precipitate of TiN is substantially square, the length d of one of its sides is used as the size of TiN, and this size of TiN was classified into a group less than 0.05 .mu.m (hereinafter called the "A rank"), a group of 0.05 to 10 .mu.m (hereinafter called the "B rank") and a group exceeding 10 .mu.m (hereinafter called the "C rank"), and the proportion of each rank was displayed by wt %.
In the drawing, when the cooling rate at the time of casting was great (82.degree. C./min), both yield point and tensile strength became great while the r value was extremely small, and cold forming was extremely difficult. TiN at this time was all in the A rank. As the cooling rate at the time of casting was decreased (38.degree. C./min), the yield point and the tensile strength gradually dropped while the elongation and the r value increased, so that cold machinability was improved. When the cooling rate at the time of casting was further lowered (7.degree. C./min), the yield point increased somewhat, the tensile strength dropped somewhat, and the elongation as well as the r value dropped. In conjunction with the size distribution of TiN, good machinability could not be obtained when the size of the A rank was too great or when the size of the C rank was too great, and formability equivalent to that of the corresponding material could be obtained when the size of the B rank was at least 50%.
The reasons are assumed as follows. When the cooling rate at the process of casting is high, TiN below 0.05 .mu.m finely precipitates, impedes the grain growth at the time of annealing and provides the action of precipitation hardening. As a result, elongation or the r value is remarkably deteriorated. When the cooling rate at the process of casting is low, on the other hand, a large amount of TiN exceeding 10 .mu.m precipitates, and cracks occur from such great inclusions in the cast.
Accordingly, elongation is mainly deteriorated. FIG. 2 shows a sketch of TiN measured by anelectron microscope. Item (1) described in FIG. 2 shows an example when the size d is about 1 .mu.m, item (2) described in FIG. 2 shows an example when the size d is about 3 .mu.m and item (3) described in FIG. 2 shows an example when d is from about 6 to about 7 .mu.m.
In other words, in order to obtain a cold rolled sheet having high formability from the starting material having a high N content, the present invention forms TiN by adding Ti, makes N harmless by limiting a free N quantity, and drastically improves the mechanical properties such as the yield point, the tensile strength, the r value, etc., by stipulating the size of TiN in a predetermined range.
Accordingly, the product according to the present invention is a cold rolled steel sheet containing not greater than 0.1% of C, 0.0060 to 0.0150% of N, not greater than 0.4% of Mn which also satisfies the relation Mn/S.gtoreq.7, not greater than 0.030% of S, not greater than 0.1% of Al, not greater than 0.08% of Ti which also satisfies the relation Ti:N (%)--Ti/3.42 (%).ltoreq.0.0070, in terms of weight percentage (wt %), and the balance consisting of Fe and unavoidable impurities, wherein the cold rolled steel sheet comprises a texture in which TiN having a size of 0.05 to 10 .mu.m (by measurement through an electron microscope) is precipitated in weight at least 1/2 of the TiN total weight.
To obtain such a cold rolled steel sheet, a molten steel having the chemical components described above is cooled at a temperature in the range of the solidifying point to 600.degree. C. at a rate of 10 to 50.degree. C./min to produce a slab, and after this slab is heated, it is hot rolled. Then, the resulting hog rolled sheet is taken up at a temperature of not lower than 700.degree. C. and is cold rolled. Thereafter, continuous annealing is carried out. Incidentally, when box annealing of the cold rolled sheet is carried out, the slab is heated at a temperature not lower than 1,130.degree. C., and after hot rolling, the sheet is wound at a temperature not higher than 650.degree. C.
When continuous annealing is carried out, Ti is added in such an amount that free N in the slab is below 0.0040%, and when box annealing is carried out, free N falls within the range of 0.0020 to 0.0070%. To fix N, B may be added, whenever necessary.

BRIEF DESCRIPTION OF THE DRAWINGS
FIGS. 1(A), 1(B), 1(C) and 1(D) are diagrams showing the relationship between the weight % of classified size of TiN and material properties; and
FIG. 2 is a diagram showing an example of measurement of the size of TiN.

BEST MODE FOR CARRYING OUT THE INVENTION
Hereinafter, the best mode for carrying out the present invention will be described in detail.
First, the reasons for limitation of the chemical components in the present invention will be explained.
Since C improves the strength of the steel but lowers its cold formability (elongation, drawability), its upper limit is set to 0.1%. Preferably, the upper limit is not greater than 0.05%.
In order to make S harmless, Mn is added in such an amount as to satisfy at least the relation Mn/S.gtoreq.7. However, when Mn is added in an excessive amount, it deteriorates formability (elongation, deep drawability). Accordingly, the upper limit is set to 0.4%.
S induces red heat brittleness during hot rolling and causes the occurrence of cracks. Therefore, its upper limit is set to 0.03%.
Al is the element which is added for deoxidation and for fixing N which has not been fixed and made harmless by Ti. However, the addition of Al in a great amount lowers elongation, and the upper limit is therefore set to 0.1%, and the lower limit is set to 0.005%. The object described above cannot be accomplished when the amount is less than this lower limit value.
N is a detrimental element for formability, but its whole amount need not be fixed by Ti and be made harmless. However, the amount of free N which is not fixed by Ti must be stipulated.
In other words, the formula N (%)--Ti/3.42 (%) must be not greater than 0.0070%. When the value exceeds 0.0070%, the precipitation quantity of AlN for fixing excessive free N becomes great, and the grain growth at the process of annealing is impeded. Accordingly, elongation and the r value drop.
As described above, Ti is added so as to fix N and to make it harmless, but an amount satisfying at least the relation N (%)--Ti/3.42 (%).ltoreq.0.0070% is necessary. However, excessive Ti bonds with C and TiC precipitates if the amount of addition is too great. In such a case, elongation and the r value become deteriorated. Accordingly, the upper limit is set to 0.08%.
B combines with N and forms BN, and provides the effect of preventing the precipitation of AlN. In the production method by continuous annealing, the precipitation state of AlN is susceptible to the influences of the temperature history at hot rolling, and results in variance of properties. To avoid this problem, high temperature winding is preferably carried out in hot rolling. The addition of B can solve this problem, and a cold rolled steel sheet having excellent deep drawability can be produced by continuous annealing without effecting high temperature winding.
The addition of B in this case is 1.0.ltoreq.1.3.times.B (%)/(N (%)--Ti (%)/3.42).ltoreq.1.5. In other words, the relation 1.3.times.B (%)/(N (%)--Ti (%)/3.42) represents the atomic ratio of B and free N, and when this value is greater than 1.0, high temperature winding can be omitted. When B is added in an amount exceeding 1.5 times the amount of free N, elongation and the r value drop. Therefore, the amount should be limited to not greater than 1.5 times.
In the present invention, the steel substantially comprises Fe with the exception of the components described above, and the steel may contain unavoidable elements which mix from the molten raw materials such as the scrap.
Next, the production condition will be described.
The molten steel having the components described above is poured into a casting machine such as a continuous casing machine and is cooled to produce a slab. In this case, cooling is carried out at a cooling rate of 10 to 50.degree. C./min within a temperature range of the solidifying point to 600.degree. C. The size of TiN in an amount at least 1/2 of the total weight is made to 0.05 to 10 .mu.m by this cooling.
Next, after being heated within an ordinary temperature range, the slab is hot rolled. The hot rolling condition is not particularly limited, but in order to obtain a cold rolled steel sheet having high deep drawability by the continuous annealing process, a winding temperature is within the range of not lower than 700.degree. C. In this case, free N (N (%)--Ti/3.42 (%)) is not greater than 0.0040%. For, when free N is below 0.0040%, N is fixed as AlN and is rendered harmless.
In order to particularly secure deep drawability for the steel sheet produced by the continuous annealing process, it is preferred to limit the free N amount to a low level (because the AlN formation time is short) and to precipitate in advance N as AlN by high temperature winding. Further, massing and granulation of the carbides are simultaneously effected by high temperature winding.
Incidentally, when B is added as described above, precipitation of AlN is not necessary, and high temperature winding of the hot rolled sheet can be omitted.
To obtain a cold rolled steel sheet having high deep drawability by the box annealing process, the heating temperature of the slab is set to at least 1.130.degree. C., and the winding temperature is set to be not greater than 650.degree. C. In this case, N (%)--Ti/3.42 (%) must be from 0.0020 to 0.0070%. In other words, to secure deep drawability for the rolled sheet by the box annealing process, a minimum 0.0020% of free N is allowed to remain and AlN is allowed to precipitate during the annealing process so that the texture structure can be improved by using this AlN, unlike the case of the production of the rolled sheet by continuous annealing. Accordingly, the slab is heated at a high temperature of at least 1,130.degree. C. so as to cause complete solid solution of AlN, and low temperature winding of the hot rolled sheet is carried out so as not to allow AlN to precipitate before the annealing step.
The cold rolling condition is not particularly limited, and ordinary rolling is carried out to obtain a desired sheet thickness.
Although the present invention has been completed on the basis of the cold rolled steel sheet, this technology can also be applied to surface treated steel sheets for containers, for construction and for automobiles as will be represented by the following examples.
EXAMPLES
Example 1
Steels having the components tabulated in Table 1 were hot rolled, cold rolled and annealed under the condition tabulated in Table 2. The properties obtained in this instance were also tabulated in Table 2.
Experiment No. 6 represents the case where free N exceeded the upper limit of claim 1 and elongation was inferior. Experiments Nos. 9 and 10 represent the cases where the sizes of TiN were too great and elongation was also inferior. Experiments Nos. 11 and 12 represent the cases where the sizes of TiN were too small, so that the yield strength was excessively high and elongation was low.
Steels Nos. 1, 2, 3, 4, 5, 7 and 8 as the steel of the present invention provided excellent properties (yield strength, tensile strength, elongation, r value).
TABLE 1__________________________________________________________________________ Free Si .times. Mn .times. P .times. Al .times. Ti .times. N* TiN**No. C ppm 10.sup.-3 % 10.sup.-3 % 10.sup.-3 % S ppm 10.sup.-3 % N ppm 10.sup.-3 % ppm Form Remarks__________________________________________________________________________1 302 9 163 5 118 32 122 29 37 a This invention2 413 25 210 8 161 55 102 32 8 a This invention3 501 16 222 6 144 60 82 20 24 a This invention4 355 10 188 8 142 54 140 25 67 a This invention5 401 8 155 5 149 35 122 49 -21 a This invention6 415 8 170 6 135 70 90 -- 90 -- Comp. Example7 310 9 165 6 121 35 118 29 33 a This invention8 310 9 165 6 121 35 118 29 33 a This invention9 410 13 199 6 142 44 109 27 30 b Comp. Example10 410 13 199 6 142 44 109 27 30 b Comp. Example11 330 15 188 7 151 46 139 37 31 c Comp. Example12 330 15 188 7 151 46 139 37 31 c Comp. Example__________________________________________________________________________ *Free N: total N - Ti/3.42 **TiN form: (a) 0.05 .mu.m .ltoreq. TiN size .ltoreq.10 .mu.m was at leas 50% of the tatal amount (b) 10 .mu.m < TiN size was at least 50% of the total amount (c) TiN size <0.05 .mu.m was at least 50% of the total amoun The underline represents the portions outside the range of the present invention.
TABLE 2__________________________________________________________________________Processing Condition Cold RollingHot Rolling Condition Condition Thickness Thickness SkinSlab of Hot Reduc- of cold PassHeating Winding Rolled tion rolled Roll-Temp. Temp. Sheet ratio sheet Annealing Condition ingNo. .degree.C. .degree.C. mm % mm System Cycle %__________________________________________________________________________1 1250 550 3.0 73 0.8 Box 680.degree. C. .times. 14 1.22 1150 750 3.5 77 0.8 Con. 820.degree. C. .times. 1 1.0.3 1250 550 3.0 73 0.8 Box 680.degree. C. .times. 14 1.24 1250 550 3.0 73 0.8 Box 680.degree. C. .times. 14 1.25 1150 750 3.5 77 0.8 Con. 820.degree. C. .times. 1 1.0.6 1250 550 3.0 73 0.8 Box 680.degree. C. .times. 14 1.27 1250 550 3.0 73 0.8 Box 680.degree. C. .times. 14 1.28 1150 750 3.5 77 0.8 Con. 820.degree. C. .times. 1 1.0.9 1250 550 3.0 73 0.8 Box 680.degree. C. .times. 14 1.210 1150 750 3.5 77 0.8 Con. 820.degree. C. .times. 1 1.0.11 1250 550 3.0 73 0.8 Box 680.degree. C. .times. 14 1.212 1150 750 3.5 77 0.8 Con. 820.degree. C. .times. 1 1.0.__________________________________________________________________________ Properties Yield Tensile Elon- This strength strength gation r invention or No. kgf/mm.sup.2 kgf/mm.sup.2 % Value Comp. Example__________________________________________________________________________ 1 17.1 31.0 46 1.81 This invention 2 18.1 31.5 45 1.78 This invention 3 17.2 30.8 46 1.83 This invention 4 18.4 31.9 43 1.71 This invention 5 18.9 32.4 42 1.67 This invention 6 19.7 33.4 38 1.52 Comp. Example 7 17.3 31.0 46 1.79 This invention 8 17.5 30.7 46 1.81 This invention 9 17.5 29.8 41 1.66 Comp. Example 10 17.8 30.2 40 1.70 Comp. Example 11 25.1 37.7 36 1.39 Comp. Example 12 25.4 38.0 35 1.42 Comp. Example__________________________________________________________________________ Annealing System Con.: Continuous annealing Box: Box annealing r Value = (r.sub.L + r.sub.C + 2r.sub.D)/4
Example 2
Steels having higher Ti contents as shown in Table 3 were hot rolled, cold rolled and annealed under the condition tabulated in Table 4. The properties of the resulting steel sheets were also tabulated in Table 4.
In Experiment No. 14, the Ti amount exceeded the upper limit stipulated in the claims, and the other components and the production condition were the same as those of Experiment No. 13. In comparison with Experiment No. 13 wherein the Ti amount was within the range of the present invention, both elongation and the r value were lower.
TABLE 3__________________________________________________________________________ Si .times. Mn .times. P .times. Al .times. Ti .times. C 10.sup.-3 10.sup.-3 10.sup.-3 10.sup.-3 N 10.sup.-3 Free N* TiN**No. ppm % % % S ppm % ppm % ppm Form Remarks__________________________________________________________________________13 318 9 203 5 240 44 148 74 -68 a This invention14 318 9 203 5 240 44 148 92 -121 a This invention__________________________________________________________________________ *Free N: total N Ti/3.42 **TiN form: (a) 0.05 .mu.m .ltoreq. TiN size .ltoreq.10 .mu.m was at leas 50% of the tatal amount (b) 10 .mu.m < TiN size was at least 50% of the total amount (c) TiN size <0.05 .mu.m was at least 50% of the total amoun The underline represents the portions outside the range of the present invention
TABLE 4__________________________________________________________________________Processing Condition Cold RollingHot Rolling Condition Condition Thickness Thickness SkinSlab of Hot Reduc- of cold PassHeating Winding Rolled tion rolled Roll-Temp. Temp. Sheet ratio sheet Annealing Condition ingNo. .degree.C. .degree.C. mm % mm System Cycle %__________________________________________________________________________13 1150 750 3.5 77 0.8 Con. 820.degree. C. .times. 1 1.0.14 1150 750 3.5 77 0.8 Con. 820.degree. C. .times. 1 1.0.__________________________________________________________________________ Properties Yield Tensile Elon- This strength strength gation r invention or No. kgf/mm.sup.2 kgf/mm.sup.2 % Value Comp. Example__________________________________________________________________________ 13 22.4 34.2 39 1.65 This invention 14 27.2 38.6 35 1.48 Comp. Example__________________________________________________________________________ Annealing System Con.: Continuous annealing Box: Box annealing r Value = (r.sub.L + r.sub.C + 2r.sub.D)/4
Example 3
B-containing steels having the components shown in Table 5 were hot rolled, cold rolled and annealed under the condition tabulated in Table 6. The properties obtained at this time are also tabulated in Table 6.
All of the steels were within the range of the present invention and exhibited excellent properties. However, the winding temperature of the hot rolled sheet in Experiment No. 17 was below the lower limit of claim 5 stipulating the condition for obtaining a steel sheet having excellent deep drawability by continuous annealing, and its yield point was somewhat higher while the r value was somewhat lower than those of Experiment No. 16 satisfying the condition of claim 5.
In Experiment No. 15 in which B was added, properties substantially equivalent to those of Experiment No. 16, wherein the winding temperature of the hot rolled sheet was within the range of claim 5, could be obtained even when the hot rolled sheet was taken up at a winding temperature below the lower limit of claim 5. In other words, it corresponded to claim 6, and a steel sheet having excellent deep drawability could be obtained by continuous annealing without limiting the winding temperature of the hot rolled sheet, by the addition of B.
TABLE 5__________________________________________________________________________ Si .times. Mn .times. P .times. Al .times. Ti .times. C 10-3 10-3 10-3 S 10-3 N 10-3 B Free N* TiN**No. ppm % % % ppm % ppm % ppm ppm Form Remarks__________________________________________________________________________15 432 9 237 19 125 35 111 31 17 20 a This invention addition B16 432 9 237 19 125 35 111 31 17 20 a This invention addition B17 302 9 163 5 118 32 122 29 -- 37 a This invention without addition__________________________________________________________________________ B *Free N: total N Ti/3.42 **TiN form: (a) 0.05 .mu.m .ltoreq. TiN size .ltoreq.10 .mu.m was at leas 50% of the tatal amount (b) 10 .mu.m < TiN size was at least 50% of the total amount (c) TiN size <0.05 .mu.m was at least 50% of the total amoun The underline represents the portions outside the range of the present invention
TABLE 6__________________________________________________________________________Processing Condition Cold RollingHot Rolling Condition Condition Thickness Thickness SkinSlab of Hot Reduc- of cold PassHeating Winding Rolled tion rolled Roll-Temp. Temp. Sheet ratio sheet Annealing Condition ingNo. .degree.C. .degree.C. mm % mm System Cycle %__________________________________________________________________________15 1150 630 3.5 77 0.8 Con. 820.degree. C. .times. 1 1.0.16 1150 750 3.5 77 0.8 Con. 820.degree. C. .times. 1 1.0.17 1150 630 3.5 77 0.8 Con. 820.degree. C. .times. 1 1.0.__________________________________________________________________________ Properties Yield Tensile Elon- This strength strength gation r invention or No. kgf/mm.sup.2 kgf/mm.sup.2 % Value Comp. Example__________________________________________________________________________ 15 17.8 32.7 45 1.68 This invention 16 17.4 32.3 46 1.70 This invention 17 20.2 33.9 42 1.51 This invention__________________________________________________________________________ Annealing System Con.: Continuous annealing Box: Box annealing r Value = (r.sub.L + r.sub.C + 2r.sub.D)/4
Example 4
Steels having the components shown in Table 7 were hot rolled, cold rolled and annealed under the condition tabulated in Table 8, and surface treatment was carried out. Properties obtained in these cases were also tabulated in Table 8.
The steel sheets according to the present invention exhibited good formability even after the surface treatment.
By the way, a plating quantity as 20 g/m.sup.2 for one surface in the case of electrogalvanizing, 50 g/m.sup.2 for one surface in the case of lead plating, and 20 g/m.sup.2 for one surface in the case of electrogalvanizing with an organic coating, and in this case, an organic coating having a thickness of 0.8 .mu.m was applied on the plating.
TABLE 7__________________________________________________________________________ Si .times. Mn .times. P .times. Al .times. Ti .times. C 10-3 10-3 10-3 S 10-3 N 10-3 B Free N* TiN**No. ppm % % % ppm % ppm % ppm ppm Form Remarks__________________________________________________________________________18 302 9 163 5 118 32 122 29 -- 37 a This invention19 302 9 163 5 118 32 122 29 -- 37 a This invention20 302 9 163 5 118 32 122 29 -- 37 a This invention21 432 9 237 19 125 35 111 31 17 20 a This invention22 302 9 163 5 118 32 122 29 -- 37 a This invention23 302 9 163 5 118 32 122 29 -- 37 a This invention__________________________________________________________________________ *Free N: total N Ti/3.42 **TiN form: (a) 0.05 .mu.m .ltoreq. TiN size .ltoreq.10 .mu.m was at leas 50% of the tatal amount (b) 10 .mu.m < TiN size was at least 50% of the total amount (c) TiN size <0.05 .mu.m was at least 50% of the total amoun The underline represents the portions outside the range of the present invention
TABLE 8__________________________________________________________________________Processing Condition Cold RollingHot Rolling Condition Condition Thickness Thickness SkinSlab of Hot Reduc- of cold Pass Sur-Heating Winding Rolled tion rolled Roll- faceTemp. Temp. Sheet Ratio sheet Annealing Condition ing TreatNo. .degree.C. .degree.C. mm % mm System Cycle % ment__________________________________________________________________________18 1250 550 3.0 73 0.8 Box 680.degree. C. .times. 14 1.2 EG19 1150 750 3.5 77 0.8 Con. 810.degree. C. .times. 1 1.0. EG20 1250 550 3.0 73 0.8 Box 680.degree. C. .times. 14 1.2 TC21 1150 750 3.5 77 0.8 Con. 810.degree. C. .times. 1 1.0. TC22 1250 550 3.0 73 0.8 Box 680.degree. C. .times. 14 1.2 WU23 1150 750 3.5 77 0.8 Con. 820.degree. C. .times. 1 1.0. WU__________________________________________________________________________ Properties This Yield Tensile Elon- invention strength strength gation r or Comp. No. kgf/mm.sup.2 kgf/mm.sup.2 % Value Example__________________________________________________________________________ 18 17.2 29.7 46 1.82 This invention 19 18.3 31.2 45 1.73 This invention 20 18.1 31.1 46 1.79 This invention 21 18.5 31.8 45 1.75 This invention 22 17.1 30.1 46 1.76 This invention 23 17.5 30.6 45 1.73 This invention__________________________________________________________________________ Annealing System Con: Continuous annealing Box: Box annealing Surface Treatment EG: electrogalvanizing TC: lead plating WU: electrogalvanizing with organic coating
Example 5
Steels having the components shown in Table 9 were hot rolled, cold rolled and annealed under the condition tabulated in Table 10, and molten zinc plating was carried out. Properties obtained in these cases were also tabulated in Table 10.
The steel sheets according to the present invention exhibited excellent properties even after the molten zinc plating treatment. By the way, the plating quantity of molten zinc plating was 100 g/m.sup.2 per surface.
TABLE 9__________________________________________________________________________ Si .times. Mn .times. P .times. Al .times. Ti .times. C 10-3 10-3 10-3 S 10-3 N 10-3 B Free N* TiN**No. ppm % % % ppm % ppm % ppm ppm Form Remarks__________________________________________________________________________24 501 12 222 6 144 60 82 24 -- 12 a Thia invention25 432 9 237 19 125 35 111 31 17 20 a This invention__________________________________________________________________________ *Free N: total N Ti/3.42 **TiN form: (a) 0.05 .mu.m .ltoreq. TiN size .ltoreq. 10 .mu.m was at least 50% of the tatal amount (b) 10 .mu.m < TiN size was at least 50% of the total amount (c) TiN size < 0.05 .mu.m was at least 50% of the total amount The underline represents the portions outside the range of the present invention
TABLE 10__________________________________________________________________________Processing Condition Cold RollingHot Rolling Condition Condition Thickness Thickness SkinSlab of Hot Reduc- of cold PassHeating Winding Rolled tion rolled Roll- SurfaceTemp. Temp. Sheet Ratio sheet Annealing Condition ing Treat-No. .degree.C. .degree.C. mm % mm System Cycle % ment__________________________________________________________________________24 1150 750 3.5 77 0.8 Con. 810.degree. C. .times. 1 1.0. GI25 1150 550 3.5 77 0.8 Con. 810.degree. C. .times. 1 1.0. GI__________________________________________________________________________ Properties Yield Tensile Elon- This strength strength gation r invention or No. kgf/mm.sup.2 kgf/mm.sup.2 % Value Comp. Example__________________________________________________________________________ 24 24.4 34.1 41 1.69 This invention 25 25.0 34.7 38 1.66 This invention__________________________________________________________________________ Annealing System Con.: Continuous annealing Box: Box Annealing Surface Treatment GI: molten zinc plating
Example 6
Steels having the components shown in Table 11 were hot rolled, cold rolled and annealed under the condition tabulated in Table 12, and electrotinning was carried out. Properties obtained in these cases were also tabulated in Table 12.
The steel sheets according to the present invention also exhibited here excellent properties as a steel sheet for a tin plate.
TABLE 11__________________________________________________________________________ Si .times. Mn .times. P .times. Al .times. Ti .times. C 10-3 10-3 10-3 S 10-3 N 10-3 Free N* TiN**No. ppm % % % ppm % ppm % ppm Form Remarks__________________________________________________________________________26 488 10 258 17 110 52 117 28 35 a This invention27 488 10 258 17 110 52 117 -- 117 a Comp. Example28 488 10 258 17 110 52 117 23 50 a This invention29 488 10 258 17 110 52 117 -- 117 a Comp. Example__________________________________________________________________________ *Free N: total N Ti/3.42 **TiN form: (a) 0.05 .mu.m .ltoreq. TiN size .ltoreq.10 .mu.m was at leas 50% of the tatal amount (b) 10 .mu.m < TiN size was at least 50% of the total amount (c) TiN size <0.05 .mu.m was at least 50% of the total amoun The underline represents the portions outside the range of the present invention
TABLE 12__________________________________________________________________________Processing Condition Cold RollingHot Rolling Condition Condition Thicknes Thickness SkinSlab of Hot Reduc- of clod Pass Properties ThisHeating Winding Rolled tion rolled Annealing roll- Surface Degree inventionTemp. Temp. Sheet ratio sheet Condition ing Treat- Hard- of or Comp.No. .degree.C. .degree.C. mm % mm System Cycle % ment ness Temper Example__________________________________________________________________________26 1235 550 3.0 90 0.3 Box 650.degree. C. .times. 1.3 ET 49 T-1 This 8 H invention27 1235 550 3.0 90 0.3 Box 650.degree. C. .times. 1.3 ET 56 T-1 Comp. 8 H Example28 1235 550 3.0 90 0.3 Con. 650.degree. C. .times. 1.3 ET 61 T-4 This 20 sec. invention29 1235 550 3.0 90 0.3 Con. 650.degree. C. .times. 1.3 ET 68 T-4 Comp. 20 sec. Example__________________________________________________________________________ *refining rolling: reduction ratio 1.3% **hardness: rockwell hardness (HR30T)
Example 7
Steels having the components shown in Table 13 were hot rolled, cold rolled and annealed under the condition tabulated in Table 14. Properties obtained in these cases were also tabulated in Table 14.
Even when those elements which were unavoidably contained in the scrap, such as Sn, Cr, Ni, etc., were contained, the effect of the present invention was not at all deteriorated. In other words, excellent formability could be obtained when the basic components, the quantity of TiN and its form were within the ranges of the present invention.
TABLE 13__________________________________________________________________________ Si .times. Mn .times. P .times. Al .times. Ti .times. Free C 10.sup.-3 10.sup.-3 10.sup.-3 S 10.sup.-3 N 10.sup.-3 B N* TiN** Cu Nl Cr As Sn MoNO. ppm % % % ppm % ppm % ppm ppm form % % % % % % Remarks__________________________________________________________________________30 302 9 163 5 118 32 122 29 -- 37 a 0.016 0.026 0.015 -- -- -- This invention31 415 8 170 6 135 70 90 0 -- 90 a -- -- -- -- -- -- Comp. Example32 432 9 237 19 125 35 111 31 -- 20 a 0.10 0.04 0.08 0.04 0.04 0.05 This invention33 302 9 163 5 118 35 122 29 -- 37 a 0.09 0.19 0.19 0.05 0.04 0.06 This invention34 401 9 165 6 121 35 118 29 -- 37 b 0.015 0.024 0.024 -- -- -- Comp. Example35 415 9 165 6 121 32 118 29 -- 33 c 0.015 0.024 0.024 -- -- -- Comp. Example__________________________________________________________________________ *Free N: total N Ti/3.42 **TiN form: (a) 0.05 .mu.m .ltoreq. TiN size .ltoreq.10 .mu.m was at leas 50% of the tatal amount (b) 10 .mu.m < TiN size was at least 50% of the total amount (c) TiN size <0.05 .mu.m was at least 50% of the total amoun The underline represents the portions outside the range of the present invention
TABLE 14__________________________________________________________________________Processing Condition Cold RollingHot Rolling Condition Condition Thickness Thickness SkinSlab of Hot reduc- of cold Pass Sur-Heating Winding Rolled tion rolled Roll- faceTemp. Temp. Sheet Ratio sheet Annealing Condition ing TreatNo. .degree.C. .degree.C. mm % mm System Cycle % ment__________________________________________________________________________30 1250 550 3.0 73 0.8 Box 680.degree. C. .times. 14 1.2 --31 1250 550 3.0 73 0.8 Box 680.degree. C. .times. 14 1.2 --32 1150 750 3.5 77 0.8 Con. 810.degree. C. .times. 1 1.0. --33 1250 550 3.0 73 0.8 Box 680.degree. C. .times. 14 1.2 --34 1250 550 3.0 73 0.8 Box 680.degree. C. .times. 14 1.2 --35 1250 550 3.0 73 0.8 Box 680.degree. C. .times. 14 1.2 --__________________________________________________________________________ Properties This Yield Tensile Elon- invention strength strength gation r or Comp. No. kgf/mm.sup.2 kgf/mm.sup.2 % value Example__________________________________________________________________________ 30 17.1 31.0 46 1.81 This invention 31 19.7 33.4 38 1.52 Comp. Example 32 18.1 32.8 44 1.68 This invention 33 17.8 32.4 44 1.70 This invention 34 17.5 32.8 42 1.66 Comp. Example 35 25.4 32.4 36 1.39 Comp. Example__________________________________________________________________________ Annealing System Con.: Continuous annealing Box: Box annealing
INDUSTRIAL APPLICABILITY
The present invention can make N harmless where N unavoidably attains a high level when a scrap is reutilized, and can obtain a cold rolled steel sheet having high formability irrespective of a high N content.
The cold rolled steel sheet according to the present invention can be utilized not only as the cold rolled steel sheet but also as a raw sheet for a surface treated steel sheet such as a molten zinc plated steel sheet, an electrogalvanized steel sheet, an electrotin plated steel sheet, and so forth. Accordingly, the present invention has an extremely great industrial value.

Claims

1. A cold rolled steel sheet having excellent formability and comprising not greater than 0.1 wt % of C, 0.0060 to 0.0150 wt % of N, not greater than 0.4 wt % of Mn (within the range satisfying the relation Mn/S.gtoreq.7), not greater than 0.030 wt % of S, 0.005 to 0.1% of Al, not greater than 0.08 wt % of Ti (within the range satisfying the relation (N (%)--Ti/3.42 (%).ltoreq.0.0070%), and the balance consisting of Fe and unavoidable impurities, wherein TiN having a size of 0.05 to 10 .mu.m is precipitated in a weight of at least 1/2 of the total TiN weight.
2. A cold rolled steel sheet according to claim 1, wherein the Ti content is within the range satisfying the relation N (%)--Ti/3.42 (%).ltoreq.0.0040%.
3. A cold rolled steel sheet according to claim 1, wherein the Ti content is within the range satisfying the relation 0.0020%.ltoreq.N (%)--Ti/3.42 (%).ltoreq.0.0070%.
4. A cold rolled steel sheet according to claim 2, which further contains B in an amount satisfying the relation 1.0.ltoreq.1.3.times.B (%)/(N (%)--Ti (%)/3.42).ltoreq.1.5.
5. A production method of a cold rolled steel sheet having excellent formability by casting a molten steel comprising not greater than 0.1 wt % of C, 0.0060 to 0.0150 wt % of N, not greater than 0.4 wt % of Mn (within the range satisfying the relation Mn/S.gtoreq.7), not greater than 0.03 wt % of S, 0.005 to 0.1 wt % of Al, not greater than 0.08 wt % of Ti (within the range satisfying the relation (N (%)--Ti/3.42 (%).ltoreq.0.0040%), and the balance consisting of Fe and unavoidable impurities, said method comprising:
cooling a resulting slab at a cooling rate of 10.degree. to 50.degree. C./min within the temperature range of a solidifying point to 600.degree. C. so as to precipitate TiN having a size of 0.05 to 10 .mu.m in a weight of at least 1/2 of the total TiN weight in the resulting slab;
heating the slab;
hot rolling the slab;
winding a resulting hot rolled steel strip at a temperature of at least 700.degree. C.;
cold rolling the hot rolled steel strip;
and
effecting then continuous annealing.
6. A production method of a cold rolled steel sheet having excellent formability, by casting a molten steel comprising not greater than 0.1 wt % of C, 0.0060 to 0.0150 wt % of N, not greater than 0.4 wt % of Mn (within the range satisfying the relation Mn/S.gtoreq.7), not greater than 0.03 wt % of S, 0.005 to 0.1 wt % of Al, not greater than 0.08 wt % of Ti (within the range satisfying the relation (N (%)--Ti/3.42 (%).ltoreq.0.0040%), B in an amount satisfying the relation 1.0.ltoreq.1.3.times.B (%)/(N (%)--Ti (%)/3.42).ltoreq.1.5 and the balance consisting of Fe and unavoidable impurities, said method comprising:
cooling a resulting slab at a cooling rate of 10.degree. to 50.degree. C./min within the temperature range of a solidifying point to 600.degree. C. so as to precipitate TiN having a size of 0.05 to 10 .mu.m in a weight of at least 1/2 of the total TiN weight in the resulting slab;
heating the slab;
hot rolling the slab;
winding a resulting hot rolled steel strip;
cold rolling the hot rolled steel strip;
and
effecting then continuous annealing.
7. A production method of a cold rolled steel sheet having excellent formability, by casting a molten steel comprising not greater than 0.1 wt % of C, 0.0060 to 0.0150 wt % of N, not greater than 0.4 wt % of Mn (within the range satisfying the relation Mn/S.gtoreq.7), not greater than 0.030 wt % of S, 0.005 to 0.1 wt % of Al, not greater than 0.08 wt % of Ti (within the range satisfying the relation 0.0020 wt %.ltoreq.N (%)--Ti/3.42 (%).ltoreq.0.0070%), and the balance consisting of Fe and unavoidable impurities, said method comprising:
cooling a resulting slab at a cooling rate of 10.degree. to 50.degree. C./min within a temperature range of a solidifying point to 600.degree. C. so as to precipitate TiN having a size of 0.05 to 10 .mu.m in a weight of at least 1/2 of the TiN total weight inside the resulting slab;
heating the slab to a temperature of not lower than 1,130.degree. C.;
hot rolling the slab;
winding a resulting hot rolled steel strip within a temperature range of not higher than 650.degree. C.;
cold rolling the hot rolled steel strip;
and
effecting then box annealing.

Priority Claims (1)

Number	Date	Country	Kind
5-260247	Oct 1993	JPX

PCT Information

Filing Document	Filing Date	Country	Kind	102e Date	371c Date
PCT/JP94/01752	10/18/1994			6/14/1995	6/14/1995

Publishing Document	Publishing Date	Country	Kind
WO95/11320	4/27/1995

US Referenced Citations (1)

Number	Name	Date	Kind
5123969	Chou	Jun 1992

Foreign Referenced Citations (8)

Number	Date	Country
44-18066	Aug 1969	JPX
53-12899	May 1978	JPX
57-26124	Feb 1982	JPX
63-45322	Feb 1988	JPX
3-54186	Aug 1991	JPX
3-267321	Nov 1991	JPX
4-292352	Oct 1992	JPX
6-136482	May 1994	JPX

Cold rolled steel having excellent machinability and production thereof

Information

Patent Number

Date Filed

Date Issued

Inventors

Original Assignees

Examiners

Agents

CPC

US Classifications

Field of Search

US