CA2041403C - Method of producing high-strength cold-rolled steel sheet suitable for working - Google Patents
Method of producing high-strength cold-rolled steel sheet suitable for workingInfo
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- CA2041403C CA2041403C CA002041403A CA2041403A CA2041403C CA 2041403 C CA2041403 C CA 2041403C CA 002041403 A CA002041403 A CA 002041403A CA 2041403 A CA2041403 A CA 2041403A CA 2041403 C CA2041403 C CA 2041403C
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- steel
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Classifications
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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
- C21D8/0431—Warm rolling
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
-
- 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
-
- 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
- C21D8/0436—Cold rolling
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
A method of producing a high-strength cold-rolled steel sheet suitable for working uses which utilizes a steel material having the following composition: not more than 0.02 wt% of C, not more than 1.0 wt% of Si, not more than 2.0 wt% of Mn, and not less than 0.01 wt% but not more than 0.10 wt% of Ti, the Ti, C and N contents being determined to meet the condition of Ti > (48/12) C wt% + (48/14) N wt%, the steel also consisting essentially of not less than 0.0010 wt% but not more than 0.0100 wt% of Nb, not less than 0.0002 wt% but not more than 0.0020 wt% of B, not less than 0.03 wt% but not more than 0.20 wt% of P, not more than 0.03 wt% of S, not less than 0.010 wt% but not more than 0.100 wt% of A?, not more than 0.008 wt% of N, not more than 0.0045 wt% of O, and the balance substantially Fe and incidental inclusions. The steel material is cast and hot-rolled and then subjected to a cold rolling conducted at a sheet temperature not higher than 300°C under such a condition that the sum of the rolling reductions of passes which meet the following condition between said sheet temperature (T °C) and the strain rate ? (S-1) is 50 % or greater:
T X ? ? 50,000°C S-1 The steel sheet is then continuously annealed or galvannealed.
T X ? ? 50,000°C S-1 The steel sheet is then continuously annealed or galvannealed.
Description
2~41403 BACKGROUND OF THE INVENTION
Field of the Invention:
The present invention relates to a method of producing a high-strength cold-rolled steel sheet suitable for various 05 types of working such as press working, bulging and so forth and adaptable also to deep drawing.
In recent years, there is an increasing demand for high-strength steel sheets in the field of automobile production, in order to meet current requirements for reduction in the weight of automobiles to attain a higher fuel economy and for ensuring safety of drivers and passengers.
In modern automobile production, high-strength cold-rolled steel sheets are used not only for the inner panels but also for outer panels such as engine hoods, trunk lid and fenders. As a consequence, high-strength cold-rolled steel sheet is required to have an excellent workability.
Description of the Related Art:
Hitherto, an art has been proposed in which, in order to improve workability of cold-rolled steel sheet, the carbon content of the steel is reduced and a carbonitride formers are added to the steel. For instance, Japanese Patent Laid-Open Publication No. 63-317648 discloses a cold-rolled steel sheet in which Ti, Nb and B are added to a low-carbon steel for the purpose of improving press-workability and spot-weldability. It has also been proposed to add strengthening elements such as P and Mn to the above-2~11403 mentioned steel system. For instance, Japanese PatentPublication No. 61-11294 discloses a method of producing a high-strength steel sheet having a superior workability in which a steel enriched with P is continuously annealed after 05 a cold rolling. Similarly, Japanese patent Publication No.
1-28817 discloses a method in which a steel enriched with P
and Mn is continuously annealed to form a high-strength cold-rolled steel sheet.
These known methods exhibit disadvantages. The method disclosed in Japanese Patent Laid-Open No. 63-317648 cannot provide required strength, while the methods disclosed in Japanese Patent Publication Nos. 61-11294 and 1-28817 inevitably reduce workability although they exhibit improved strength. Under these circumstances, steel sheets superior both in strength and workability are strongly demanded.
SUMMARY 0~ THE INVENTION
An object of the present invention is to provide a method of producing, from a low-carbon steel having an extremely small carbon content, a high-strength cold-rolled steel sheet suitable for working, and more particularly a steel sheet having a superior workability, specifically a Lankford value (r) of 1.8 or greater, a tensile strength T.S.) of 40 kgf/mm2 or greater, an elongation (E~) of 40 %
or greater, and a truncated-cone height of 40 mm or greater in the conical cup test.
To this end, according to the present invention, there is provided a method of producing a high-strength cold-rolled steel sheet suitable for working, comprising the stepsof:
preparing a steel consisting essentially of not more than 0.02 wt% of C, not more than 1.0 wt% of Si, not more than 2.0 wt% of Mn, and not less than 0.01 wt% but not more than 0.10 wt% of Ti, the Ti, C and N contents being determined to meet the condition of Ti ~ ~48/12) C wt% +
(48/14) N wt%, not less than 0.0010 wt% but not more than 0.0100 wt% of Nb, not less than 0.0002 wt% but not more than 0.0020 wt% of B, not less than 0.03 wt% but not more than 0.20 wt% of P, not more than 0.03 wt% of S, not less than 0.010 wt% but not more than 0.100 wt% of AQ, not more than 0.008 wt% of N, not more than 0.0045 wt% of 0, and the balance substantially Fe and incidental inclusions;
subjecting the steel to an ordinary casting, reheating the steel to a temperature not lower than 1,100C.
not higher than 1,250C., and a subsequent conventional hot-rolling;
subjecting the hot-rolled steel to a cold rolling conducted at a sheet temperature not higher than 300C under such a condition that the sum of the rolling reductions of passes in which the sheet temperature (TC) and a strain rate (S 1) meet the following condition:
T X ~ ~ 50,000C S
is 50% or greater; and subjecting the cold-rolled steel to a continuous annealing.
The sheet temperature T (C) is the temperature of -the steel sheet at positions immediately downstream from the cold-rolling stands as measured by an infrared pyrometer, while the strain rate is calculated in accordance with the following formula:
= (2 n n/60 ~ ) X ~ ~ ) X ~n[1/(1 - r)]
where, n represents the roll peripheral speed (rpm), Ho represents the sheet thickness at inlet side, r represents the rolling reduction and R represents the radius of the roll.
DESCRIPTION OF THE DRAWING
Fig. 1 is a graph which shows the relationship between rolling reductions and various characteristics of the steel sheet.
DETAILED DESCRIPTION OF THE INVENTION
Through an intense study on improvement in workability of high-strength cold-rolled steel sheet, the inventors have found that a high-strength cold-rolled steel sheet having a superior workabilityr specifically a Lankford value (r) of 1.8 or greater, preferably 2.1 or greaterr 20 especially preferably 2.1 to 2.3r a tensile strength (T.S.) of 40 kgf/mm2 or greaterr preferably 40 to 54.3 kgf/mm2, an elongation (E~) of 40 % or greater, preferably 40 to 50.3 %
and a truncated-cone height of 40 mm or greater, preferably 40 to 55 mm, can be obtained by selecting the strain-imparting condition in the cold B-2041~03 rolling of a very-low-carbon steel which is rich in P and small in oxygen content.
The present invention is based upon the above-described discovery. A description will be given first of the reason 05 why the condition is posed that the sum of the rolling reductions of passes which meet the condition of T X _ 50,000OC S-l between the sheet temperature (T C) and the strain rate ~ (S-l) is 50 % or greater.
Three types of continuous-cast steel slabs A,B and C
having the compositions shown in Table 1 were prepared by a converter.
TA~LE 1 Steel Contents (wt%) type Symbols C Si Mn P S A~ N Ti Nb 13 0 Ti*
A 0.0025 0.010.25 0.0750.008 0.0550.00220.0320.0040.00120.0031 0.014 }3 0.0025 0.010.22 0.0150.007 0.0480.00280.0330.0040.00110.0033 0.013 C O .0024 0.010.25 0.0770. OOû 0.0~70.00230.0330.0040.00110.007~ 0.016 Ti*=Ti-(48/12) C-(48/14) N
o 20~140~
-Each slab was heated to 12500C and rough-rolled at a rolling reduction of 88 %, followed by a hot finish-rolling at a rolling reduction of 88 % (hot-rolling finish temperature : 880C, coiling temperature: 500C) so as to be formed into a hot coil of 4.0 mm thick. Then, an ordinary cold rolling was effected at a rolling reduction of 82.5 %
so that the steel was formed into a sheet 0.7 mm thick.
Subsequently, a continuous annealing was conducted at 810C
followed by a temper rolling at a rolling reduction of 0.8 %, thereby producing a rolled steel sheet.
The cold rolling was conducted~while varying the sheet temperature within the range of 30C to 3000C, while varying the reduction rate, i.e,, the strain rate ~ within the range between 10 S-l to 2,000 S-l. The sheet temperature was controlled by varying the initial sheet temperature for the cold rolling and the flow rate of the cooling water.
The Lankford value (r), elongation, tensile strength and truncated-cone height were measured for each of the sample steel sheets. The truncated-cone height, which is an index indicative of the workability approximating that in actual working was measured by a conical cup test conducted under the following conditions:
punch diameter: 80 mm die diameter : 140 mm ~
wrinkle pressing force: 10 t Fig. 1 shows the relationship between these measured values and the sum of the rolling reductions of the passes which meet the condition of the product of the cold rolling sheet temperature and the strain rate being not smaller than 50,000OC S-l.
As will be clearly understood from Fig. 1, the low-05 oxygen steel material A rich in P exhibited a tensilestrength (T.S.) which is smaller than that of the steel B
which has a small P content. In addition, when the sum of the rolling reductions of the passes having the product of the sheet temperature and the strain rate being 50,000 oc S-1 or greater is 50% or above, the truncated-cone height indicative of the workability approximating that of actual working is remarkably improved to a value approximating that of the steel B which has a large tensile strength, while the elongation(E~) and the Lankford value (r) increase only slightly.
The steel C which is rich both in P and C does not show remarkable improvement in the properties indicative of the workability such as the Lankford value (r), elongation (E~) and the truncated-cone height.
In order to produce a high-strength cold-rolled steel sheet having superior workability, therefore, it is necessary to use a low-oxygen material ha-ving a large P
content and that the cold rolling is conducted under a condition which meets the condition of the sum of the rolling reductions of the passes having the product of the sheet temperature and the strain rate being 50,000 C S-l or greater is 50% or greater.
In conventional cold rolling of steel sheets, the sum of the rolling reductions of passes which meet the condition of the product of the sheet temperature and the strain rate being 50,000 oc S-l or greater is generally around 30 %. In 05 order to raise the value of the sum of the rolling reductions, it is necessary to take suitable measures such as an increase in the rolling speed, control of flow rate of cooling water, or elevation of the initial cold rolling temperature through a continuous change from the preceding step, which is usually pickling.
According to the invention,it is possible to obtain a high-strength cold-rolled steel having high workability by using a low-oxygen steel rich in P as the material and by conducting the cold rolling under the specific condition mentioned above. The reason why such superior workability is obtained has not been clarified yet.
The reason, however, is considered to reside in the following fact. In general, a microscopic observation of structure of a steel sheet rich in P exhibits a segregation zone in the thicknesswise central region of the sheet. In contrast, the steel produced by the method of the present invention does not exhibit such a degradation zone. This suggests that a certain effect which could not be produced by the conventional methods is caused on the segregation zone by the cold rolling condition peculiar to the invention. Although the reason is still unknown, it is considered that the cold rolling condition peculiar to the invention produces a uniform working effect in the 20~1403 thicknesswise direction so that a greater rolling effect is produced on the segregation zone as compared to known methods.
The segregation zone does not produce any substantial OS unfavorable effect on the elongation Lankford value (r) which is measured in tensile test. In the actual use of the material, however, the segregation zone reduces the uniformity of the steel sheet in the thicknesswise direction and, hence, is considered to cause a reduction in the workability.
According to the method of the present invention, however, the cold rolling conducted under the specified condition produces a working effect which serves to break the segregation zone, so that the uniformity of the structure in the thicknesswise direction of the steel sheet is improved so as to improve the workability as confirmed through the conical cup test which simulates the actual condition of use. When the oxygen content in the steel is large, however, the large quantity of the inclusions impedes the cold-rolling straining of P in the segregation zone so as to reduce the effect of improving the workability.
A description will now be given of the reason for limitation of the chemical composition of the steel.
C: C serves, when added to the steel material together with Ti, to strengthens the steel without impairing workability.
When the C content exceeds 0.02 wt%, however, effect of improving the workability is saturated even when the content of Ti is increased. The upper limit of C content,therefore, -is determined to be 0.02 wt%. In order to obtain an excellent workability,therefore, the C content is preferably below 0.006 wt%.
Si: The upper limit of Si content is set to be 1.0 wt%, 05 since the drawing characteristic of the steel is impaired when the Si content exceeds 1.0 wt%.
Mn: This element is effective in raising the strength~
without impairing the drawing characteristic. Addition of this element in an excessive amount reduces the drawing characteristic so that the Mn content is limited to be not more than 2.0 wt%.
Ti: This element serves to fix C and N in the steel so as to prevent deterioration of the material caused by solid solution of C. In addition, this element impedes formation of BN so as to prevent reduction in the amount of solid solution of B. In order to obtain an appreciable effect, therefore, this element should be added in an amount exceeding the sum of the C equivalent [(48/12) C wt%] and N
equivalent [(48/14) N wt%]. However, Ti content below 0.01 wt% is too low to enable Ti to produce any appreciable effect. On the other hand, addition of Ti in excess of 0.10 wt% reduces the strength. Therefore, the Ti content should be not less than 0.01 wt% and not more that 0.10 wt% and be determined to exceed the value of [(48/12) C wt% + (48/14) N
wt%].
Nb: This element is essential since it improves the Lankford value (r) and strengthens the steel when added together with B. Nb content below 0.0010 wt%, however,does not produce 2041~03 any remarkable effect. On the other hand,addition of Nb in excess of 0.0100 wt% reduces the workability so as to impair the balance between strength and workability. The Nb content,therefore,is determined to be not less than 0.0010 05 wt% but not more than 0.0100 wt%. When the steel is bound to be a deep drawing, however, the Nb content is preferably not less than 0.0075 wt%.
B: This element is indispensable since it improves the strength when added together with Nb. B content below 0.0002 wt% does not produce any remarkable effect, while addition of B in excess of 0.002 wt% seriously degrades the material. The B content, therefore, is determined to be not less than 0.0002 wt% but not more than 0.002 wt%.
Preferably, B content is determined to be not more than 0.0012 wt%.
P: This element is an important strengthening element. The effect of this element is remarkable particularly when the content is 0.03 wt% or more. However, addition of P in excess of 0.20 wt% deteriorates the balance between strength and workability and, in addition, causes an undesirable effect on the brittleness of the steel. The content of P, therefore, is determined to be not less than 0.03 wt% but not more than 0.20 wt%, more preferably not less than 0.04 wt% but not more than 0.15 wt%.
S: A reduction in S content in the steel is necessary for improving deep drawability. However, the undesirable effect on the workability produced by S is not so serious when the -S content is reduced down below 0.03 wt%. The upper limit of the S content is therefore set to be 0.03 wt%.
Ae: This element is necessary for improving yield of carbonitride formers through deoxidation and for eliminating 05 generation of surface defects caused by formation of TiO2.
The effect of addition of this element, however, is not appreciable when the content is below 0.010 wt%. In addition, the deoxidation effect is saturated when the Ae content is increased beyond 0.10 wt%. In addition, increase in the Ae content tends to cause surface defect due to generation of Ae2O3. The Ae content, therefore, is determined to be not less than 0.01 wt% but not more than 0.10 wt%.
N: This element degrades deep drawability of the steel and, in addition, reduces anti-secondary working embrittlement due to bonding with B, unless it is fixed by Ti. Thus, a greater N content uneconomically requires greater amount of Ti. The N content,therefore, should be not more than 0.008 wt%, preferably not more than 0.006 wt%.
O: In order to improve workability which is the critical requirement in the present invention, it is necessary to reduce O concentration. When the O content exceeds 0.0045 wt%, the cold-rolling straining to the segregation zone is impeded by a large amount of inclusions as explained before.
As a consequence, the effect of improving workability produced by the cold straining is impaired and, in addition, an effect which is not negligible is caused on the brittleness. For this reason, the upper limit of O content is set to be 0.0045 wt%, preferably to 0.004 wt%.
Reduction in the oxygen content in the steel is effected by controlling the length of time of killed treatment in degassing step in ordinary steel making process.
05 A description will now be given of the preferred condition for the preparation of the starting steel material having the above-described composition and preferred condition for the production of a steel sheet from the starting steel material.
The steel making process and a subsequent hot rolling can be carried out in the same manner as the known process, except that the oxygen content is reduced by the method described above.
A material having satisfactory properties can be obtained when the coiling temperature of the steel after the hot rolling falls within the range of ordinary process, e.g., between 4000C and 7000C. Thus, it is not necessary to employ a specifically high coiling temperature. Rather, it is preferred that the coiling temperature is comparatively low, e.g., 5500C or less, in order to avoid any deterioration in pickling property caused by the thickening of scale and to prevent excessive softening of the product.
The co - rolling may be conducted by using an ordinary cold rolling mill, provided that the aforementioned cold rolling condition is met. Namely, it is necessary that the sum of the rolling reductions of passes which meets the condition of the product of the sheet temperature and the strain rate being not smaller than 50,000 oc S-l is 50 % or greater. There is no restriction in the total rolling reduction, i.e.,the sum of the reductions of all passes employed, provided that the above-described condition is 05 met.
As stated before, the cold rolling sheet temperature has to be not higher than 300OC because a cold rolling at higher temperature causes concentration of shear deformation to the surface region of the steel sheet, making it difficult to work the central segregation zone.
When the steel having the described composition is annealed by batch-type box annealing method, the steel tends to become brittle due to grain boundary segregation of P due to high P content, particularly when the cooling rate is small. In order to obviate this problem, according to the present invention, a continuous annealing method which enables rapid heating and cooling. The annealing temperature, however, may be not lower than recrystallization temperature but not higher than A3 transformation temperature, as in the case of ordinary steel annealing process.
The temper rolling subsequent to the annealing may be effected under ordinary steel tempering condition with a rolling reduction corresponding to the sheet thickness (mm), for the purpose of, for example, obtaining optimum shape of the sheet.
Example Ten types of steels, including 7 types meeting the composition condition of the invention and 3 types as reference examples, were prepared in a converter and were continuously cast into slabs. Each slab was hot-rolled to os form a hot coil of 3,0 mm thick and cold-rolled to a thickness of 0.72 mm. Subsequently, a continuous annealing was conducted under ordinary condition. Then, the steel sheets other than the type No. 3 were subjected to a temper rolling with a rolling reduction of 0.7 ~, whereby 10 types of steel sheets including one which has not been subjected to temper rolling were prepared.
The roll used in the cold rolling had a diameter of 600 mm. The cold rolling speed was 1500 to 2500 m/min at the outlet side of the cold rolling stand.
Among ten types of steel, each of type Nos. 1 and 2 were subjected to three different production conditions with different cold-rolling and continuous annealing conditions,so that three samples were produced for each of the steel type Nos. 1 and 2. Similarly, two samples were prepared from the steel type No. 1 through different production conditions. Only one sample was prepared for each of the remainder steel types.
Table 3 shows the hot-rolling and continuous annealing conditions, Table 4 shows the cold rolling conditions and Table 5 shows the result of examination of the properties of the cold-rolled sample steel sheets.
Steel Contents (wt%) type Class No. C Si Mn P S Ae N Ti Nb B O Ti*
1 Invention 0.00210.01 0.11 0.0550.0080.0400.00250.0320.00340.00080.0025 0.015 2 Invention 0.00260.02 0.45 0.0730.0120.0390.00270.0420.00240.00070.0019 0.022 3 Invention 0.00200.03 0.09 0.1300.0060.0810.00310.0720.00440.00100.0037 0.053 4 Invention 0.00290.02 0.33 0.0840.0050.0360.00150.0360.00700.00090.0033 0.019 Invention 0.00560.25 0.29 0.0850;0180.0240.00430.0510.00200.00060.0028 0.014 6 Invention 0.00800.02 0.34 0.0620.0270.0650.00510.0570.00990.00160.0036 0.008 C 7 Invention 0.00350.76 1.54 0.0420.0170.0350.00210.0610.00480.00110.0030 0.040 8 Comp. Ex. 0.00340.01 0.34 0.0600.0150.0500.00220.0450.00320.00120.0054 0.024 9 Comp. $x. 0.00300.02 0.24 0.0880.0100.0600.00190.0150.00250.00100.0034 -0.004 Comp. Ex. 0.00210.05 0.33 0.0680.0220.0610.00340.0380.02500.00050.0037 0.018 Comp. Ex.=Comparative Example Ti*=Ti-(48/12) C-(48/14) N
o o Continuous annealing condition Steel Slab Hot-roll , , Sample t e Classheating finishing Colllng CR* Re-Max heating No. No.temp- (C) temp. (C) temp- ( C) crystallization temp. (C) 1 1 Invention 1200 920 480 77 770 790 2 1 Comp. Ex. 1200 920 480 34 770 790 3 1 Invention 1200 920 480 68 770*1 790 4 2 Invention 1150 910 500 61 780 810 2 Comp. Ex. 1150 910 500 40 780 810 6 2 Comp. Ex. 1150 910 500 *2 118 780 810 7 3 Invention 1100 900 550 62 800 850 8 4 Invention 1250 900 550 62 770 780 9 4 Comp. Ex. 1250 900 550 26 770 780 Invention 1200 880 600 55 750 880 11 6 Invention 1200 850 650 65 730 850 12 7 Invention 1250 890 550 51 760 850 13 8 Comp. Ex. 1200 900 550 63 770 800 14 9 Comp. Ex. 1200 900 550 65 770 800 O
Comp. Ex. 1200 900 550 63 770 800 ~_~
Comp. Ex.=Comparative Example CR*: Sum of rolling reductions of paths which meets condition of sheet temp.(T)xstrain rate(~)_50,000Cs~1 C~3 *1: Continuous hot-dip galvanizing line used *2: Sheet temp. in cold-rolling exceeded 300C
20~1403 TABLE 4 ( 1 ) Sam- Steel Stand No. CR*
ple type Class Items No.No. 1 2 3 4 5 6 (%
Rolling re- 37 47 24 5 - _ 76 duction (%) 1 1 Inven T (C) 50 100 130 140 -tion(s-l) 4001,1701,280 650 Tx(Cs 1) 20,000 117,000 166,000 91,000 Rolliny re- 57 19 19 15 - - 34 2 1Comp.T (C) 45 75 100 120 Ex.~ (s-l) 750 620 850 980 TX(Cs~l) 34,00047,000 85,000 117,000 duction (%) 42 18 8 - _ 68 3 1Inven T (C) 55 90 115 130 -tion (S-l) 430 960 850 630 TX(Cs 1) 24,000 87,00098,00082,000 - - -Rolliny re- 17 40 40 17 4 - 61 duction (%) 4 2Inven T (C) 50 80 100 120 130 -tion ~ (5-l) 160 5201,120 960 500 Tx(Cs ) 8,000 42,000 112,000 115,000 65,000 dRolling (r%e) 48 29 14 14 12 - 40 T (C) 30 60 90 120 140 2Comp.
Ex. ( -1~ 610 810 690 860 990 - -Tx~tCs 1)18,00048,000 62,000 103,000 139,000 Rolling re-43 35 18 11 10 - 117*
ductlon (%) T (C) 350 350 350 360 360 6 2Comp.
Ex. ~ (s 1) 310 530 520 480 540 TX~(Cs 1) 109,000 186,000 181,000 174,000 194,000 duction (%) 47 44 18 3 - - 62 7 3 Inven T (C)55 90 110 120 -tion ~480 1,110 960 390 Tx~(Cs 1) 27,000 100,000 106,000 47,000 Comp. Ex.=Comparative Example *Sheet temp. 300C or above.
TALLE 4 (2) Sam- Steel Stand No.
ple type Class Items CR*
No. No. 1 2 3 4 5 6 (%) Rolling re- 33 28 28 19 12 4 63 Inven T (C) 40 70 70 120 130 140 -t1on (5-l) 350 520 840 960 910 570 T X ~ ( Cs 1)14,000 36,00059,000 116,000 119,000 79,000 Rolling re-33 25 23 17 17 9 26 duction (%) 9 4 Comp. T (C) 30 50 70 80 90 100 Ex. (s~l) 250 340 490 560 730 610 Tx~(Cs 1)8,00017,00034,00045,00066,00061,000 Rolling re-33 33 30 18 8 - 56 duction (~) Inven T (C) 40 80 120 140 150 -tion (s~l)340600 970 1020 760 TX~(Cs 1)13,000 48,000 117,000 143,000 113,000 duction (%) 48 39 13 8 5 - 65 11 6Inven T (C) 35 70 100 110 120 -tlon ~ (s 1) 490 920 650 610 520 TX~(Cs 1) 17,00065,00065,00067,00062,000 Rolling re- 33 35 35 9 6 - 50 12 7Inven T (C) 40 70 100 130 140 -tion (S-l)350 690 1290 790 720 Tx~(Cs 1)14,000 48,000 129,000 102,000 101,000 Rolling re-33 28 2421 14 4 63 duction ( ~ ) 13 8 Comp. T (C) 40 60 80100 120 130 Ex. ~ (s~l) 310 460 650860 870 500 TX~(Cs 1)12,00027,00052,00086,000 104,000 65,000 Rolling re-48 39 13 8 5 - 65 14 9Comp. T (C) 35 70 100 110 120 Ex. ~ (s ) 490 920 650 610 520 Tx~(Cs 1)17,00065,00065,00067,000 62,000 duction (~) 33 28 24 21 14 4 63 10 Comp. T ( C) 40 60 80 100 120 130 Ex. (5-l)310 460 650 860 870 500 TX~(Cs 1)12,00027,000 52,000 86,000 104,000 65,000 CR* : Sum of rolling reductions of paths vhich meets condition of sheet temp.(T)Xstrain rate(~j~50,000Cs 1 Comp. Ex.=Comparative Example TABLE 5 Comp. Ex.=Comparative Example N P type Class (kgf/mls2) (kg~/mm2) k-~; T.S.~E~. r value crne t~ei~ht 1 1 Invention 20.0 35.4 50.3 85.7 2.2 55 2 1 Comp. Ex. 20.4 35.4 50.5 85.9 2.2 30 3 1 Invention 20.6 36.2 49.6 85.8 2.1 51 4 2 Invention 21.2 38.6 47.5 86.1 2.2 55 2 Comp. Ex. 22.5 38.5 47.5 86.0 2.2 25 6 2 Comp. Ex. 22.7 38.8 45.5 84.3 2.0 20 7 3 Invention 25.8 45.2 41.2 86.4 2.1 55 8 4 Invention 20.7 36.5 49.2 85.7 2.3 50 9 4 Comp. Ex. 20.9 36.1 49.1 85.2 2.2 33 Invention 23.3 40.5 45.3 85.8 2.1 52 11 6 Invention 28.1 48.5 36.4 85.1 2.0 45 12 7 Invention 24.9 54.3 33.4 87.7 2.0 53 13 8 Comp. Ex. 21.5 35.4 49.4 84.8 2.0 35 O
14 9 Comp. Ex. 26.4 34.8 42.1 76.9 1.6 20 ~-~
10 Comp. Ex. 22.0 36.1 43.1 79.2 2.0 30 O
From Table 5, it will be understood that the Sample Nos. 2, 5, 6, 9, 13, 14 and 15 as reference examples showed comparatively small values of truncated-cone height ranging from 20 mm to 35 mm. In contrast, other samples which meet the condition of the invention showed large values of truncated-cone height ranging from 45 mm to 55 mm, thus proving superior workability.
Sample No. 3 was subjected to a galvannealing instead of the continuous annealing. This galvannealed steel sheet also showed excellent workability as in the cases of other samples meeting the conditions of the invention.
Sample No. 6 was cold-rolled at a cold-rolling sheet temperature exceeding 300C, although the sum of the rolling reductions of the passes having the product of the sheet temperature and the strain rate exceeding 50,000~C S 1 was greater than 50 %. Consequently, this sample showed a too small workability which was 20 mm in terms of truncated-cone height.
The truncated-cone height was obtained by a conventional conical cup test as follows. A truncated cone-shaped test sample was first prepared by punching a sheet with a punch having a diameter of 80 mm for a die with a diameter of 140 mm. In this case, when a Y value was low or a YS value was high, a wrinkle was produced in a tapered portion of the test sample and when an n value was low, a crack was produced in a top corner portion of the test sample.
A critical height at which molding could be carried out without producing a wrinkle or crack in the test sample was defined as truncated-cone height.
As will be understood from the foregoing description, a method has been established by the present invention which enables production of a high-strength cold-rolled steel sheet having superior workability by processing a low-oxygen low-carbon steel rich in P under specific cold-rolling conditions. The cold-rolled steel sheet produced by the method of the invention is suitable for use as a material of products which are produced through press-forming, bulging, deep-drawing and other plastic works.
~~ 73461-24 .~ ~
Field of the Invention:
The present invention relates to a method of producing a high-strength cold-rolled steel sheet suitable for various 05 types of working such as press working, bulging and so forth and adaptable also to deep drawing.
In recent years, there is an increasing demand for high-strength steel sheets in the field of automobile production, in order to meet current requirements for reduction in the weight of automobiles to attain a higher fuel economy and for ensuring safety of drivers and passengers.
In modern automobile production, high-strength cold-rolled steel sheets are used not only for the inner panels but also for outer panels such as engine hoods, trunk lid and fenders. As a consequence, high-strength cold-rolled steel sheet is required to have an excellent workability.
Description of the Related Art:
Hitherto, an art has been proposed in which, in order to improve workability of cold-rolled steel sheet, the carbon content of the steel is reduced and a carbonitride formers are added to the steel. For instance, Japanese Patent Laid-Open Publication No. 63-317648 discloses a cold-rolled steel sheet in which Ti, Nb and B are added to a low-carbon steel for the purpose of improving press-workability and spot-weldability. It has also been proposed to add strengthening elements such as P and Mn to the above-2~11403 mentioned steel system. For instance, Japanese PatentPublication No. 61-11294 discloses a method of producing a high-strength steel sheet having a superior workability in which a steel enriched with P is continuously annealed after 05 a cold rolling. Similarly, Japanese patent Publication No.
1-28817 discloses a method in which a steel enriched with P
and Mn is continuously annealed to form a high-strength cold-rolled steel sheet.
These known methods exhibit disadvantages. The method disclosed in Japanese Patent Laid-Open No. 63-317648 cannot provide required strength, while the methods disclosed in Japanese Patent Publication Nos. 61-11294 and 1-28817 inevitably reduce workability although they exhibit improved strength. Under these circumstances, steel sheets superior both in strength and workability are strongly demanded.
SUMMARY 0~ THE INVENTION
An object of the present invention is to provide a method of producing, from a low-carbon steel having an extremely small carbon content, a high-strength cold-rolled steel sheet suitable for working, and more particularly a steel sheet having a superior workability, specifically a Lankford value (r) of 1.8 or greater, a tensile strength T.S.) of 40 kgf/mm2 or greater, an elongation (E~) of 40 %
or greater, and a truncated-cone height of 40 mm or greater in the conical cup test.
To this end, according to the present invention, there is provided a method of producing a high-strength cold-rolled steel sheet suitable for working, comprising the stepsof:
preparing a steel consisting essentially of not more than 0.02 wt% of C, not more than 1.0 wt% of Si, not more than 2.0 wt% of Mn, and not less than 0.01 wt% but not more than 0.10 wt% of Ti, the Ti, C and N contents being determined to meet the condition of Ti ~ ~48/12) C wt% +
(48/14) N wt%, not less than 0.0010 wt% but not more than 0.0100 wt% of Nb, not less than 0.0002 wt% but not more than 0.0020 wt% of B, not less than 0.03 wt% but not more than 0.20 wt% of P, not more than 0.03 wt% of S, not less than 0.010 wt% but not more than 0.100 wt% of AQ, not more than 0.008 wt% of N, not more than 0.0045 wt% of 0, and the balance substantially Fe and incidental inclusions;
subjecting the steel to an ordinary casting, reheating the steel to a temperature not lower than 1,100C.
not higher than 1,250C., and a subsequent conventional hot-rolling;
subjecting the hot-rolled steel to a cold rolling conducted at a sheet temperature not higher than 300C under such a condition that the sum of the rolling reductions of passes in which the sheet temperature (TC) and a strain rate (S 1) meet the following condition:
T X ~ ~ 50,000C S
is 50% or greater; and subjecting the cold-rolled steel to a continuous annealing.
The sheet temperature T (C) is the temperature of -the steel sheet at positions immediately downstream from the cold-rolling stands as measured by an infrared pyrometer, while the strain rate is calculated in accordance with the following formula:
= (2 n n/60 ~ ) X ~ ~ ) X ~n[1/(1 - r)]
where, n represents the roll peripheral speed (rpm), Ho represents the sheet thickness at inlet side, r represents the rolling reduction and R represents the radius of the roll.
DESCRIPTION OF THE DRAWING
Fig. 1 is a graph which shows the relationship between rolling reductions and various characteristics of the steel sheet.
DETAILED DESCRIPTION OF THE INVENTION
Through an intense study on improvement in workability of high-strength cold-rolled steel sheet, the inventors have found that a high-strength cold-rolled steel sheet having a superior workabilityr specifically a Lankford value (r) of 1.8 or greater, preferably 2.1 or greaterr 20 especially preferably 2.1 to 2.3r a tensile strength (T.S.) of 40 kgf/mm2 or greaterr preferably 40 to 54.3 kgf/mm2, an elongation (E~) of 40 % or greater, preferably 40 to 50.3 %
and a truncated-cone height of 40 mm or greater, preferably 40 to 55 mm, can be obtained by selecting the strain-imparting condition in the cold B-2041~03 rolling of a very-low-carbon steel which is rich in P and small in oxygen content.
The present invention is based upon the above-described discovery. A description will be given first of the reason 05 why the condition is posed that the sum of the rolling reductions of passes which meet the condition of T X _ 50,000OC S-l between the sheet temperature (T C) and the strain rate ~ (S-l) is 50 % or greater.
Three types of continuous-cast steel slabs A,B and C
having the compositions shown in Table 1 were prepared by a converter.
TA~LE 1 Steel Contents (wt%) type Symbols C Si Mn P S A~ N Ti Nb 13 0 Ti*
A 0.0025 0.010.25 0.0750.008 0.0550.00220.0320.0040.00120.0031 0.014 }3 0.0025 0.010.22 0.0150.007 0.0480.00280.0330.0040.00110.0033 0.013 C O .0024 0.010.25 0.0770. OOû 0.0~70.00230.0330.0040.00110.007~ 0.016 Ti*=Ti-(48/12) C-(48/14) N
o 20~140~
-Each slab was heated to 12500C and rough-rolled at a rolling reduction of 88 %, followed by a hot finish-rolling at a rolling reduction of 88 % (hot-rolling finish temperature : 880C, coiling temperature: 500C) so as to be formed into a hot coil of 4.0 mm thick. Then, an ordinary cold rolling was effected at a rolling reduction of 82.5 %
so that the steel was formed into a sheet 0.7 mm thick.
Subsequently, a continuous annealing was conducted at 810C
followed by a temper rolling at a rolling reduction of 0.8 %, thereby producing a rolled steel sheet.
The cold rolling was conducted~while varying the sheet temperature within the range of 30C to 3000C, while varying the reduction rate, i.e,, the strain rate ~ within the range between 10 S-l to 2,000 S-l. The sheet temperature was controlled by varying the initial sheet temperature for the cold rolling and the flow rate of the cooling water.
The Lankford value (r), elongation, tensile strength and truncated-cone height were measured for each of the sample steel sheets. The truncated-cone height, which is an index indicative of the workability approximating that in actual working was measured by a conical cup test conducted under the following conditions:
punch diameter: 80 mm die diameter : 140 mm ~
wrinkle pressing force: 10 t Fig. 1 shows the relationship between these measured values and the sum of the rolling reductions of the passes which meet the condition of the product of the cold rolling sheet temperature and the strain rate being not smaller than 50,000OC S-l.
As will be clearly understood from Fig. 1, the low-05 oxygen steel material A rich in P exhibited a tensilestrength (T.S.) which is smaller than that of the steel B
which has a small P content. In addition, when the sum of the rolling reductions of the passes having the product of the sheet temperature and the strain rate being 50,000 oc S-1 or greater is 50% or above, the truncated-cone height indicative of the workability approximating that of actual working is remarkably improved to a value approximating that of the steel B which has a large tensile strength, while the elongation(E~) and the Lankford value (r) increase only slightly.
The steel C which is rich both in P and C does not show remarkable improvement in the properties indicative of the workability such as the Lankford value (r), elongation (E~) and the truncated-cone height.
In order to produce a high-strength cold-rolled steel sheet having superior workability, therefore, it is necessary to use a low-oxygen material ha-ving a large P
content and that the cold rolling is conducted under a condition which meets the condition of the sum of the rolling reductions of the passes having the product of the sheet temperature and the strain rate being 50,000 C S-l or greater is 50% or greater.
In conventional cold rolling of steel sheets, the sum of the rolling reductions of passes which meet the condition of the product of the sheet temperature and the strain rate being 50,000 oc S-l or greater is generally around 30 %. In 05 order to raise the value of the sum of the rolling reductions, it is necessary to take suitable measures such as an increase in the rolling speed, control of flow rate of cooling water, or elevation of the initial cold rolling temperature through a continuous change from the preceding step, which is usually pickling.
According to the invention,it is possible to obtain a high-strength cold-rolled steel having high workability by using a low-oxygen steel rich in P as the material and by conducting the cold rolling under the specific condition mentioned above. The reason why such superior workability is obtained has not been clarified yet.
The reason, however, is considered to reside in the following fact. In general, a microscopic observation of structure of a steel sheet rich in P exhibits a segregation zone in the thicknesswise central region of the sheet. In contrast, the steel produced by the method of the present invention does not exhibit such a degradation zone. This suggests that a certain effect which could not be produced by the conventional methods is caused on the segregation zone by the cold rolling condition peculiar to the invention. Although the reason is still unknown, it is considered that the cold rolling condition peculiar to the invention produces a uniform working effect in the 20~1403 thicknesswise direction so that a greater rolling effect is produced on the segregation zone as compared to known methods.
The segregation zone does not produce any substantial OS unfavorable effect on the elongation Lankford value (r) which is measured in tensile test. In the actual use of the material, however, the segregation zone reduces the uniformity of the steel sheet in the thicknesswise direction and, hence, is considered to cause a reduction in the workability.
According to the method of the present invention, however, the cold rolling conducted under the specified condition produces a working effect which serves to break the segregation zone, so that the uniformity of the structure in the thicknesswise direction of the steel sheet is improved so as to improve the workability as confirmed through the conical cup test which simulates the actual condition of use. When the oxygen content in the steel is large, however, the large quantity of the inclusions impedes the cold-rolling straining of P in the segregation zone so as to reduce the effect of improving the workability.
A description will now be given of the reason for limitation of the chemical composition of the steel.
C: C serves, when added to the steel material together with Ti, to strengthens the steel without impairing workability.
When the C content exceeds 0.02 wt%, however, effect of improving the workability is saturated even when the content of Ti is increased. The upper limit of C content,therefore, -is determined to be 0.02 wt%. In order to obtain an excellent workability,therefore, the C content is preferably below 0.006 wt%.
Si: The upper limit of Si content is set to be 1.0 wt%, 05 since the drawing characteristic of the steel is impaired when the Si content exceeds 1.0 wt%.
Mn: This element is effective in raising the strength~
without impairing the drawing characteristic. Addition of this element in an excessive amount reduces the drawing characteristic so that the Mn content is limited to be not more than 2.0 wt%.
Ti: This element serves to fix C and N in the steel so as to prevent deterioration of the material caused by solid solution of C. In addition, this element impedes formation of BN so as to prevent reduction in the amount of solid solution of B. In order to obtain an appreciable effect, therefore, this element should be added in an amount exceeding the sum of the C equivalent [(48/12) C wt%] and N
equivalent [(48/14) N wt%]. However, Ti content below 0.01 wt% is too low to enable Ti to produce any appreciable effect. On the other hand, addition of Ti in excess of 0.10 wt% reduces the strength. Therefore, the Ti content should be not less than 0.01 wt% and not more that 0.10 wt% and be determined to exceed the value of [(48/12) C wt% + (48/14) N
wt%].
Nb: This element is essential since it improves the Lankford value (r) and strengthens the steel when added together with B. Nb content below 0.0010 wt%, however,does not produce 2041~03 any remarkable effect. On the other hand,addition of Nb in excess of 0.0100 wt% reduces the workability so as to impair the balance between strength and workability. The Nb content,therefore,is determined to be not less than 0.0010 05 wt% but not more than 0.0100 wt%. When the steel is bound to be a deep drawing, however, the Nb content is preferably not less than 0.0075 wt%.
B: This element is indispensable since it improves the strength when added together with Nb. B content below 0.0002 wt% does not produce any remarkable effect, while addition of B in excess of 0.002 wt% seriously degrades the material. The B content, therefore, is determined to be not less than 0.0002 wt% but not more than 0.002 wt%.
Preferably, B content is determined to be not more than 0.0012 wt%.
P: This element is an important strengthening element. The effect of this element is remarkable particularly when the content is 0.03 wt% or more. However, addition of P in excess of 0.20 wt% deteriorates the balance between strength and workability and, in addition, causes an undesirable effect on the brittleness of the steel. The content of P, therefore, is determined to be not less than 0.03 wt% but not more than 0.20 wt%, more preferably not less than 0.04 wt% but not more than 0.15 wt%.
S: A reduction in S content in the steel is necessary for improving deep drawability. However, the undesirable effect on the workability produced by S is not so serious when the -S content is reduced down below 0.03 wt%. The upper limit of the S content is therefore set to be 0.03 wt%.
Ae: This element is necessary for improving yield of carbonitride formers through deoxidation and for eliminating 05 generation of surface defects caused by formation of TiO2.
The effect of addition of this element, however, is not appreciable when the content is below 0.010 wt%. In addition, the deoxidation effect is saturated when the Ae content is increased beyond 0.10 wt%. In addition, increase in the Ae content tends to cause surface defect due to generation of Ae2O3. The Ae content, therefore, is determined to be not less than 0.01 wt% but not more than 0.10 wt%.
N: This element degrades deep drawability of the steel and, in addition, reduces anti-secondary working embrittlement due to bonding with B, unless it is fixed by Ti. Thus, a greater N content uneconomically requires greater amount of Ti. The N content,therefore, should be not more than 0.008 wt%, preferably not more than 0.006 wt%.
O: In order to improve workability which is the critical requirement in the present invention, it is necessary to reduce O concentration. When the O content exceeds 0.0045 wt%, the cold-rolling straining to the segregation zone is impeded by a large amount of inclusions as explained before.
As a consequence, the effect of improving workability produced by the cold straining is impaired and, in addition, an effect which is not negligible is caused on the brittleness. For this reason, the upper limit of O content is set to be 0.0045 wt%, preferably to 0.004 wt%.
Reduction in the oxygen content in the steel is effected by controlling the length of time of killed treatment in degassing step in ordinary steel making process.
05 A description will now be given of the preferred condition for the preparation of the starting steel material having the above-described composition and preferred condition for the production of a steel sheet from the starting steel material.
The steel making process and a subsequent hot rolling can be carried out in the same manner as the known process, except that the oxygen content is reduced by the method described above.
A material having satisfactory properties can be obtained when the coiling temperature of the steel after the hot rolling falls within the range of ordinary process, e.g., between 4000C and 7000C. Thus, it is not necessary to employ a specifically high coiling temperature. Rather, it is preferred that the coiling temperature is comparatively low, e.g., 5500C or less, in order to avoid any deterioration in pickling property caused by the thickening of scale and to prevent excessive softening of the product.
The co - rolling may be conducted by using an ordinary cold rolling mill, provided that the aforementioned cold rolling condition is met. Namely, it is necessary that the sum of the rolling reductions of passes which meets the condition of the product of the sheet temperature and the strain rate being not smaller than 50,000 oc S-l is 50 % or greater. There is no restriction in the total rolling reduction, i.e.,the sum of the reductions of all passes employed, provided that the above-described condition is 05 met.
As stated before, the cold rolling sheet temperature has to be not higher than 300OC because a cold rolling at higher temperature causes concentration of shear deformation to the surface region of the steel sheet, making it difficult to work the central segregation zone.
When the steel having the described composition is annealed by batch-type box annealing method, the steel tends to become brittle due to grain boundary segregation of P due to high P content, particularly when the cooling rate is small. In order to obviate this problem, according to the present invention, a continuous annealing method which enables rapid heating and cooling. The annealing temperature, however, may be not lower than recrystallization temperature but not higher than A3 transformation temperature, as in the case of ordinary steel annealing process.
The temper rolling subsequent to the annealing may be effected under ordinary steel tempering condition with a rolling reduction corresponding to the sheet thickness (mm), for the purpose of, for example, obtaining optimum shape of the sheet.
Example Ten types of steels, including 7 types meeting the composition condition of the invention and 3 types as reference examples, were prepared in a converter and were continuously cast into slabs. Each slab was hot-rolled to os form a hot coil of 3,0 mm thick and cold-rolled to a thickness of 0.72 mm. Subsequently, a continuous annealing was conducted under ordinary condition. Then, the steel sheets other than the type No. 3 were subjected to a temper rolling with a rolling reduction of 0.7 ~, whereby 10 types of steel sheets including one which has not been subjected to temper rolling were prepared.
The roll used in the cold rolling had a diameter of 600 mm. The cold rolling speed was 1500 to 2500 m/min at the outlet side of the cold rolling stand.
Among ten types of steel, each of type Nos. 1 and 2 were subjected to three different production conditions with different cold-rolling and continuous annealing conditions,so that three samples were produced for each of the steel type Nos. 1 and 2. Similarly, two samples were prepared from the steel type No. 1 through different production conditions. Only one sample was prepared for each of the remainder steel types.
Table 3 shows the hot-rolling and continuous annealing conditions, Table 4 shows the cold rolling conditions and Table 5 shows the result of examination of the properties of the cold-rolled sample steel sheets.
Steel Contents (wt%) type Class No. C Si Mn P S Ae N Ti Nb B O Ti*
1 Invention 0.00210.01 0.11 0.0550.0080.0400.00250.0320.00340.00080.0025 0.015 2 Invention 0.00260.02 0.45 0.0730.0120.0390.00270.0420.00240.00070.0019 0.022 3 Invention 0.00200.03 0.09 0.1300.0060.0810.00310.0720.00440.00100.0037 0.053 4 Invention 0.00290.02 0.33 0.0840.0050.0360.00150.0360.00700.00090.0033 0.019 Invention 0.00560.25 0.29 0.0850;0180.0240.00430.0510.00200.00060.0028 0.014 6 Invention 0.00800.02 0.34 0.0620.0270.0650.00510.0570.00990.00160.0036 0.008 C 7 Invention 0.00350.76 1.54 0.0420.0170.0350.00210.0610.00480.00110.0030 0.040 8 Comp. Ex. 0.00340.01 0.34 0.0600.0150.0500.00220.0450.00320.00120.0054 0.024 9 Comp. $x. 0.00300.02 0.24 0.0880.0100.0600.00190.0150.00250.00100.0034 -0.004 Comp. Ex. 0.00210.05 0.33 0.0680.0220.0610.00340.0380.02500.00050.0037 0.018 Comp. Ex.=Comparative Example Ti*=Ti-(48/12) C-(48/14) N
o o Continuous annealing condition Steel Slab Hot-roll , , Sample t e Classheating finishing Colllng CR* Re-Max heating No. No.temp- (C) temp. (C) temp- ( C) crystallization temp. (C) 1 1 Invention 1200 920 480 77 770 790 2 1 Comp. Ex. 1200 920 480 34 770 790 3 1 Invention 1200 920 480 68 770*1 790 4 2 Invention 1150 910 500 61 780 810 2 Comp. Ex. 1150 910 500 40 780 810 6 2 Comp. Ex. 1150 910 500 *2 118 780 810 7 3 Invention 1100 900 550 62 800 850 8 4 Invention 1250 900 550 62 770 780 9 4 Comp. Ex. 1250 900 550 26 770 780 Invention 1200 880 600 55 750 880 11 6 Invention 1200 850 650 65 730 850 12 7 Invention 1250 890 550 51 760 850 13 8 Comp. Ex. 1200 900 550 63 770 800 14 9 Comp. Ex. 1200 900 550 65 770 800 O
Comp. Ex. 1200 900 550 63 770 800 ~_~
Comp. Ex.=Comparative Example CR*: Sum of rolling reductions of paths which meets condition of sheet temp.(T)xstrain rate(~)_50,000Cs~1 C~3 *1: Continuous hot-dip galvanizing line used *2: Sheet temp. in cold-rolling exceeded 300C
20~1403 TABLE 4 ( 1 ) Sam- Steel Stand No. CR*
ple type Class Items No.No. 1 2 3 4 5 6 (%
Rolling re- 37 47 24 5 - _ 76 duction (%) 1 1 Inven T (C) 50 100 130 140 -tion(s-l) 4001,1701,280 650 Tx(Cs 1) 20,000 117,000 166,000 91,000 Rolliny re- 57 19 19 15 - - 34 2 1Comp.T (C) 45 75 100 120 Ex.~ (s-l) 750 620 850 980 TX(Cs~l) 34,00047,000 85,000 117,000 duction (%) 42 18 8 - _ 68 3 1Inven T (C) 55 90 115 130 -tion (S-l) 430 960 850 630 TX(Cs 1) 24,000 87,00098,00082,000 - - -Rolliny re- 17 40 40 17 4 - 61 duction (%) 4 2Inven T (C) 50 80 100 120 130 -tion ~ (5-l) 160 5201,120 960 500 Tx(Cs ) 8,000 42,000 112,000 115,000 65,000 dRolling (r%e) 48 29 14 14 12 - 40 T (C) 30 60 90 120 140 2Comp.
Ex. ( -1~ 610 810 690 860 990 - -Tx~tCs 1)18,00048,000 62,000 103,000 139,000 Rolling re-43 35 18 11 10 - 117*
ductlon (%) T (C) 350 350 350 360 360 6 2Comp.
Ex. ~ (s 1) 310 530 520 480 540 TX~(Cs 1) 109,000 186,000 181,000 174,000 194,000 duction (%) 47 44 18 3 - - 62 7 3 Inven T (C)55 90 110 120 -tion ~480 1,110 960 390 Tx~(Cs 1) 27,000 100,000 106,000 47,000 Comp. Ex.=Comparative Example *Sheet temp. 300C or above.
TALLE 4 (2) Sam- Steel Stand No.
ple type Class Items CR*
No. No. 1 2 3 4 5 6 (%) Rolling re- 33 28 28 19 12 4 63 Inven T (C) 40 70 70 120 130 140 -t1on (5-l) 350 520 840 960 910 570 T X ~ ( Cs 1)14,000 36,00059,000 116,000 119,000 79,000 Rolling re-33 25 23 17 17 9 26 duction (%) 9 4 Comp. T (C) 30 50 70 80 90 100 Ex. (s~l) 250 340 490 560 730 610 Tx~(Cs 1)8,00017,00034,00045,00066,00061,000 Rolling re-33 33 30 18 8 - 56 duction (~) Inven T (C) 40 80 120 140 150 -tion (s~l)340600 970 1020 760 TX~(Cs 1)13,000 48,000 117,000 143,000 113,000 duction (%) 48 39 13 8 5 - 65 11 6Inven T (C) 35 70 100 110 120 -tlon ~ (s 1) 490 920 650 610 520 TX~(Cs 1) 17,00065,00065,00067,00062,000 Rolling re- 33 35 35 9 6 - 50 12 7Inven T (C) 40 70 100 130 140 -tion (S-l)350 690 1290 790 720 Tx~(Cs 1)14,000 48,000 129,000 102,000 101,000 Rolling re-33 28 2421 14 4 63 duction ( ~ ) 13 8 Comp. T (C) 40 60 80100 120 130 Ex. ~ (s~l) 310 460 650860 870 500 TX~(Cs 1)12,00027,00052,00086,000 104,000 65,000 Rolling re-48 39 13 8 5 - 65 14 9Comp. T (C) 35 70 100 110 120 Ex. ~ (s ) 490 920 650 610 520 Tx~(Cs 1)17,00065,00065,00067,000 62,000 duction (~) 33 28 24 21 14 4 63 10 Comp. T ( C) 40 60 80 100 120 130 Ex. (5-l)310 460 650 860 870 500 TX~(Cs 1)12,00027,000 52,000 86,000 104,000 65,000 CR* : Sum of rolling reductions of paths vhich meets condition of sheet temp.(T)Xstrain rate(~j~50,000Cs 1 Comp. Ex.=Comparative Example TABLE 5 Comp. Ex.=Comparative Example N P type Class (kgf/mls2) (kg~/mm2) k-~; T.S.~E~. r value crne t~ei~ht 1 1 Invention 20.0 35.4 50.3 85.7 2.2 55 2 1 Comp. Ex. 20.4 35.4 50.5 85.9 2.2 30 3 1 Invention 20.6 36.2 49.6 85.8 2.1 51 4 2 Invention 21.2 38.6 47.5 86.1 2.2 55 2 Comp. Ex. 22.5 38.5 47.5 86.0 2.2 25 6 2 Comp. Ex. 22.7 38.8 45.5 84.3 2.0 20 7 3 Invention 25.8 45.2 41.2 86.4 2.1 55 8 4 Invention 20.7 36.5 49.2 85.7 2.3 50 9 4 Comp. Ex. 20.9 36.1 49.1 85.2 2.2 33 Invention 23.3 40.5 45.3 85.8 2.1 52 11 6 Invention 28.1 48.5 36.4 85.1 2.0 45 12 7 Invention 24.9 54.3 33.4 87.7 2.0 53 13 8 Comp. Ex. 21.5 35.4 49.4 84.8 2.0 35 O
14 9 Comp. Ex. 26.4 34.8 42.1 76.9 1.6 20 ~-~
10 Comp. Ex. 22.0 36.1 43.1 79.2 2.0 30 O
From Table 5, it will be understood that the Sample Nos. 2, 5, 6, 9, 13, 14 and 15 as reference examples showed comparatively small values of truncated-cone height ranging from 20 mm to 35 mm. In contrast, other samples which meet the condition of the invention showed large values of truncated-cone height ranging from 45 mm to 55 mm, thus proving superior workability.
Sample No. 3 was subjected to a galvannealing instead of the continuous annealing. This galvannealed steel sheet also showed excellent workability as in the cases of other samples meeting the conditions of the invention.
Sample No. 6 was cold-rolled at a cold-rolling sheet temperature exceeding 300C, although the sum of the rolling reductions of the passes having the product of the sheet temperature and the strain rate exceeding 50,000~C S 1 was greater than 50 %. Consequently, this sample showed a too small workability which was 20 mm in terms of truncated-cone height.
The truncated-cone height was obtained by a conventional conical cup test as follows. A truncated cone-shaped test sample was first prepared by punching a sheet with a punch having a diameter of 80 mm for a die with a diameter of 140 mm. In this case, when a Y value was low or a YS value was high, a wrinkle was produced in a tapered portion of the test sample and when an n value was low, a crack was produced in a top corner portion of the test sample.
A critical height at which molding could be carried out without producing a wrinkle or crack in the test sample was defined as truncated-cone height.
As will be understood from the foregoing description, a method has been established by the present invention which enables production of a high-strength cold-rolled steel sheet having superior workability by processing a low-oxygen low-carbon steel rich in P under specific cold-rolling conditions. The cold-rolled steel sheet produced by the method of the invention is suitable for use as a material of products which are produced through press-forming, bulging, deep-drawing and other plastic works.
~~ 73461-24 .~ ~
Claims (9)
1. A method of producing a high-strength cold-rolled steel sheet suitable for working, comprising the steps of:
preparing a steel consisting essentially of not more than 0.02 wt% of C, not more than 1.0 wt% of Si, not more than 2.0 wt% of Mn, not less than 0.01 wt% but not more than 0.10 wt% of Ti, the Ti, C and N contents being determined to meet the condition of Ti > (48/12) C wt% +
(48/14) N wt%, not less than 0.0010 wt% but not more than 0.0100 wt% of Nb, not less than 0.0002 wt% but not more than 0.0020 wt% of B, not less than 0.03 wt% but not more than 0.20 wt% of P, not more than 0.03 wt% of S, not less than 0.010 wt% but not more than 0.100 wt% of A?, not more than 0.008 wt% of N, not more than 0.0045 wt% of 0, and the balance substantially Fe and incidental inclusions;
subjecting the steel to an ordinary casting, reheating the steel at a temperature not lower than 1,100°C.
but not higher than 1,250°C., and a subsequent conventional hot-rolling;
subjecting the hot-rolled steel to a cold rolling conducted at a sheet temperature not higher than 300°C under such a condition that the sum of the rolling reductions of passes in which the sheet temperature (T°C) and a strain rate ?(S-1) meet the following condition:
T X ? ? 50,000°C S-1 (wherein the strain rate ? (S-1) is calculated in accordance with the formula:
? = (2 IIn/60?) X (?) X ?n[1/(1 - r)]
wherein:
n represents a roll peripheral speed (rpm), H0 represents a sheet thickness at an inlet side, r represents a rolling reduction, and R represents a radius of a roll) is 50 % or greater; and subjecting the cold-rolled steel to a continuous annealing, thereby obtaining the required high-strength cold-rolled steel sheet suitable for working having a Lankford value (?) of not lower than 2.1, a tensile strength (T.S.) of not lower than 40 kfg/mm2, an elongation (E?) of not less than 40 % and a truncated-cone height not smaller than 40 mm in the conical cup test.
preparing a steel consisting essentially of not more than 0.02 wt% of C, not more than 1.0 wt% of Si, not more than 2.0 wt% of Mn, not less than 0.01 wt% but not more than 0.10 wt% of Ti, the Ti, C and N contents being determined to meet the condition of Ti > (48/12) C wt% +
(48/14) N wt%, not less than 0.0010 wt% but not more than 0.0100 wt% of Nb, not less than 0.0002 wt% but not more than 0.0020 wt% of B, not less than 0.03 wt% but not more than 0.20 wt% of P, not more than 0.03 wt% of S, not less than 0.010 wt% but not more than 0.100 wt% of A?, not more than 0.008 wt% of N, not more than 0.0045 wt% of 0, and the balance substantially Fe and incidental inclusions;
subjecting the steel to an ordinary casting, reheating the steel at a temperature not lower than 1,100°C.
but not higher than 1,250°C., and a subsequent conventional hot-rolling;
subjecting the hot-rolled steel to a cold rolling conducted at a sheet temperature not higher than 300°C under such a condition that the sum of the rolling reductions of passes in which the sheet temperature (T°C) and a strain rate ?(S-1) meet the following condition:
T X ? ? 50,000°C S-1 (wherein the strain rate ? (S-1) is calculated in accordance with the formula:
? = (2 IIn/60?) X (?) X ?n[1/(1 - r)]
wherein:
n represents a roll peripheral speed (rpm), H0 represents a sheet thickness at an inlet side, r represents a rolling reduction, and R represents a radius of a roll) is 50 % or greater; and subjecting the cold-rolled steel to a continuous annealing, thereby obtaining the required high-strength cold-rolled steel sheet suitable for working having a Lankford value (?) of not lower than 2.1, a tensile strength (T.S.) of not lower than 40 kfg/mm2, an elongation (E?) of not less than 40 % and a truncated-cone height not smaller than 40 mm in the conical cup test.
2. A method according to Claim 1, wherein the P
content is not less than 0.04 wt% and not more than 0.15 wt%
and the 0 content is not more than 0.0040 wt%.
content is not less than 0.04 wt% and not more than 0.15 wt%
and the 0 content is not more than 0.0040 wt%.
3. A method according to Claim 1, wherein galvannealing is conducted in place of the continuous annealing.
4. A method according to Claim 1, wherein:
the steel sheet is adapted for use in the production of a panel of an automobile;
the steel has the following composition (wt%):
C: 0.002 - 0.02, Si: 0.01 - 1.0, Mn: 0.09 - 2.0, Ti: 0.01 - 0.1, Nb: 0.001 - 0.01, B: 0.0002 - 0.002, P: 0.03 - 0.2, S: 0.005 - 0.03, A?: 0.01 - 0.1, N: 0.0015 - 0.008, O: 0.0019 - 0.0045, and the balance of substantially Fe and incidental inclusions;
and the sheet temperature T (°C) is the temperature of the steel sheet at a position immediately downstream from stands of the cold rolling as measured by an infrared pyrometer.
the steel sheet is adapted for use in the production of a panel of an automobile;
the steel has the following composition (wt%):
C: 0.002 - 0.02, Si: 0.01 - 1.0, Mn: 0.09 - 2.0, Ti: 0.01 - 0.1, Nb: 0.001 - 0.01, B: 0.0002 - 0.002, P: 0.03 - 0.2, S: 0.005 - 0.03, A?: 0.01 - 0.1, N: 0.0015 - 0.008, O: 0.0019 - 0.0045, and the balance of substantially Fe and incidental inclusions;
and the sheet temperature T (°C) is the temperature of the steel sheet at a position immediately downstream from stands of the cold rolling as measured by an infrared pyrometer.
5. A method according to claim 4, wherein the high-strength cold-rolled steel sheet has a Lankford value (r) o 2.1-2.3, a tensile strength (T.S.) of 40-54.3 kgf/mm2, an elongatlon (E?) of 40-50.3% and a truncated-cone height of 40-55 mm in the conical cup test.
6. A method according to claim 5, wherein:
the hot-rolling is conducted at a temperature of about 1,250°C followed by a hot finish-rolling at a temperature of about 880°C, and the so hot-rolled sheet is coiled at a temperature of 400 to 700°C;
the sheet temperature of the cold-rolling is from 30 to 300°C; and the continuous annealing is conducted at a temperature not lower than recrystallization temperature but not higher than A3 transformation temperature.
the hot-rolling is conducted at a temperature of about 1,250°C followed by a hot finish-rolling at a temperature of about 880°C, and the so hot-rolled sheet is coiled at a temperature of 400 to 700°C;
the sheet temperature of the cold-rolling is from 30 to 300°C; and the continuous annealing is conducted at a temperature not lower than recrystallization temperature but not higher than A3 transformation temperature.
7. A method according to claim 4, 5 or 6, wherein the steel contains 0.0056-0.02 wt% C.
8. A method according to claim 4, 5 or 6, wherein the steel contains 0.042-0.130 wt% P.
9. A method according to claim 4, 5 or 6, wherein the steel contains:
0.0056 - 0.02 wt% C, 0.042 - 0.130 wt% P, and 0.012 - 0.027 wt% S.
0.0056 - 0.02 wt% C, 0.042 - 0.130 wt% P, and 0.012 - 0.027 wt% S.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2159856A JPH0756051B2 (en) | 1990-06-20 | 1990-06-20 | Manufacturing method of high strength cold rolled steel sheet for processing |
| JP159856/90 | 1990-06-20 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CA2041403A1 CA2041403A1 (en) | 1991-12-21 |
| CA2041403C true CA2041403C (en) | 1997-04-22 |
Family
ID=15702727
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002041403A Expired - Lifetime CA2041403C (en) | 1990-06-20 | 1991-04-29 | Method of producing high-strength cold-rolled steel sheet suitable for working |
Country Status (6)
| Country | Link |
|---|---|
| EP (1) | EP0462380B1 (en) |
| JP (1) | JPH0756051B2 (en) |
| KR (1) | KR930004809B1 (en) |
| AU (1) | AU632228B2 (en) |
| CA (1) | CA2041403C (en) |
| DE (1) | DE69123088T2 (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2742769B1 (en) * | 1995-12-20 | 1998-01-16 | Lorraine Laminage | COLD-ROLLED STEEL WITH GOOD WELDING AND BRAZING ABILITY |
| DE19915633A1 (en) * | 1999-04-07 | 2000-10-12 | Volkswagen Ag | Turning bearing for front axle of front-wheel-drive vehicle, with sheet-metal and other components made of titanium alloy |
| KR100729125B1 (en) * | 2005-12-28 | 2007-06-14 | 현대하이스코 주식회사 | High strength steets which have good average plastic strain ratio and the method of developing those steels |
Family Cites Families (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5819442A (en) * | 1981-07-27 | 1983-02-04 | Nippon Kokan Kk <Nkk> | Manufacture of high strength cold rolled steel plate for working by continuous annealing |
| JPS5884923A (en) * | 1981-11-16 | 1983-05-21 | Nippon Steel Corp | Rolling method for unidirectional electrical steel plate of high magnetic flux density and low iron loss |
| JPS6045689B2 (en) * | 1982-02-19 | 1985-10-11 | 川崎製鉄株式会社 | Method for manufacturing cold rolled steel sheet with excellent press formability |
| JPS59193221A (en) * | 1983-04-15 | 1984-11-01 | Nippon Steel Corp | Rreparation of cold rolled steel plate used in ultra-deep drawing having extremely excellent secondary processability |
| US4676844A (en) * | 1985-03-06 | 1987-06-30 | Kawasaki Steel Corporation | Production of formable thin steel sheet excellent in ridging resistance |
| JPS61276927A (en) * | 1985-05-31 | 1986-12-06 | Kawasaki Steel Corp | Production of cold rolled steel sheet having good deep drawability |
| JPS6386819A (en) * | 1986-09-30 | 1988-04-18 | Kawasaki Steel Corp | Production of cold rolled steel sheet for deep drawing |
| US4889566A (en) * | 1987-06-18 | 1989-12-26 | Kawasaki Steel Corporation | Method for producing cold rolled steel sheets having improved spot weldability |
-
1990
- 1990-06-20 JP JP2159856A patent/JPH0756051B2/en not_active Expired - Fee Related
-
1991
- 1991-04-26 DE DE69123088T patent/DE69123088T2/en not_active Expired - Lifetime
- 1991-04-26 AU AU75971/91A patent/AU632228B2/en not_active Expired
- 1991-04-26 EP EP91106841A patent/EP0462380B1/en not_active Expired - Lifetime
- 1991-04-29 CA CA002041403A patent/CA2041403C/en not_active Expired - Lifetime
- 1991-05-10 KR KR1019910007515A patent/KR930004809B1/en not_active IP Right Cessation
Also Published As
| Publication number | Publication date |
|---|---|
| DE69123088D1 (en) | 1996-12-19 |
| KR920000957A (en) | 1992-01-29 |
| EP0462380A3 (en) | 1993-10-06 |
| EP0462380B1 (en) | 1996-11-13 |
| EP0462380A2 (en) | 1991-12-27 |
| AU7597191A (en) | 1992-01-02 |
| JPH0452230A (en) | 1992-02-20 |
| AU632228B2 (en) | 1992-12-17 |
| DE69123088T2 (en) | 1997-03-06 |
| CA2041403A1 (en) | 1991-12-21 |
| KR930004809B1 (en) | 1993-06-08 |
| JPH0756051B2 (en) | 1995-06-14 |
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