JP2000001741A - Steel sheet for deep drawing and porcelain enameling, excellent in surface characteristic and fishscale resistance, and its manufacture - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a steel sheet excellent in surface characteristic and fishscale resistance, and its manufacture. SOLUTION: The steel sheet contains, by weight, >0.010-0.200% C, <=1.0% Si, <=3.0% Mn, <=0.15% P, <=0.05% S, 0.005-1.0% Cu, >=0.0001% O, <=0.02% N, >=0.015% Ti, and >=0.0005% Ca and/or metallic REM and also contains 0.005-0.2 wt.% non-oxide Ti (Ti*) and At in an amount satisfying (1) wt.%Ti/wt.%Al>=5 or (2) Al<=0.010% and wt.%Ti/wt.%Al<5. At the time of its manufacture, a slab is heated and soaked at 900 to 1,300 deg.C, finish rolling is finished at 650 to 960 deg.C, coiling is done at 400 to 750 deg.C, cold rolling is carried out at 50 to 95% draft, and the resultant sheet is subjected to recrystallization annealing at 700 to 920 deg.C.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a steel sheet for deep drawing enamel having good surface properties and excellent anti-sticking property and a method for producing the same, and more particularly to controlling oxide-based inclusions in steel.
That is, the formation of large cluster-like inclusions was suppressed,
By dispersing into fine inclusions with a size of μm or less, while improving the toe skipping resistance and the surface properties of the steel sheet, by controlling the grain growth after hot rolling or cold rolling-annealing. It is an object of the present invention to provide an ultra-low carbon enameled steel sheet having improved strength-elongation balance.

[0002]

2. Description of the Related Art Steel is initially deoxidized with ferrotitanium as disclosed in Japanese Patent Publication No. 44-18066. However, in recent years, in order to produce steel with stable oxygen concentration at low cost, Al deoxidized steel that is deoxidized with Al has become mainstream.

[0003] Al deoxidation of steel is a method of aggregating generated oxides and separating them by flotation using a gas agitator or an RH degassing apparatus. In this case, Al ₂ O ₃ oxide is contained in a slab. Will inevitably remain. In addition, since Al ₂ O ₃ is in a cluster form, it is difficult to separate, and sometimes cluster-like inclusions of several hundred μm or more remain. If such cluster-like inclusions are trapped in the surface layer of the slab,
It will lead to surface defects like sleevers,
It is a fatal defect in enameled steel sheets that require beauty. In addition, Al deoxidation has a problem in that Al ₂ O ₃ adheres to an inner wall of an immersion nozzle used for injecting the material from a tundish into a mold, causing nozzle clogging.

[0004] In order to solve the above-mentioned problems associated with Al deoxidation, a method has been proposed in which Ca is added to aluminum-killed molten steel to produce a CaO, Al ₂ O ₃ composite oxide. (For example, Japanese Patent Application Laid-Open No. 61-276756,
58-1554447 and JP-A-6-49523). The purpose of the addition of Ca in this method is to solve the above-described problem by reacting Al ₂ O ₃ with Ca to form a low melting point composite oxide such as CaOAl ₂ O ₃ , 12CaOAl ₂ O ₃ , 3CaOAl ₂ O _3. We are trying to overcome the point.

[0005] However, when Ca is added to molten steel,
The Ca reacts with S in the steel to form CaS, and the CaS causes rust. In this regard, in Japanese Patent Application Laid-Open No. 6-559, in order to prevent rusting, the amount of Ca remaining in steel is reduced to 5 pp.
It proposes a method to reduce the concentration to m or more and less than 10 ppm. But,
Even if the Ca content is less than 10 ppm, CaO remaining in the steel
When the composition of -al ₂ O ₃ based oxide is not proper, especially in the case of CaO concentrations oxide 30% or more, its solubility S in the oxides increases, inclusions within the perimeter at the time and the solidification temperature drop To CaS
Is inevitably generated. As a result, rust is generated from the CaS as a starting point, leading to deterioration of the surface properties of the product plate. Also, if surface treatment such as plating or painting is performed while such rusting points remain, surface unevenness will inevitably occur after the treatment. On the other hand, if the high and the concentration of Al ₂ O ₃ CaO concentration is as low as 20% or less in inclusions, in particular Al ₂ O
_{3 When the} concentration is 70% or more, the melting point of inclusions increases,
Since inclusions are easily sintered, not only nozzle clogging is liable to occur during continuous casting, but also barges and slivers are generated on the surface of the steel sheet, which causes a problem that the surface properties are remarkably deteriorated.

On the other hand, in recent years, a method of deoxidizing with Ti without adding Al has been developed as JP-A-8-239731. The method of such Al-less Ti deoxidation is as follows:
Compared to the Al deoxidation method, the reached oxygen concentration is higher and the amount of inclusions is larger, but no cluster oxide is generated. In particular, the form of the inclusions generated is Ti oxide-Al ₂ O ₃ system, ₂ ~ 50μ
It exhibits a state in which about m granular oxides are dispersed. Therefore, the above-mentioned surface defects due to inclusions being clustered are reduced. However, in the case of this Ti deoxidation, in the molten steel with Al ≤ 0.005 wt%, when the Ti concentration becomes 0.010 wt% or more, the solid state Ti oxide adheres to the inner surface of the tundish nozzle by taking in the metal. There was a new problem of growing and instead causing nozzle blockage.

In order to solve such a problem (prevention of nozzle blockage), Japanese Patent Laid-Open No. 8-281391 discloses an Al-less Ti
In deoxidized steel, a method has been proposed to prevent the growth of Ti ₂ O ₃ growing on the inner surface of the nozzle by limiting the oxygen content of molten steel passing through the nozzle. However, in this method, there is another problem that the treatment amount is limited (about 800 tons) because the limitation of the oxygen amount is also limited. Also,
The fact is that the level control of the molten metal level in the mold becomes unstable with the progress of the blockage, so that it is not a fundamental solution.

The technique disclosed in Japanese Patent Application Laid-Open No. 8-281390 discloses a technique for preventing blockage of a tundish nozzle.
By the composition of inclusions by optimizing the Si concentration of the molten steel Ti ₃ O ₅ -SiO ₂ system, it has proposed a method of preventing the growth of Ti ₂ O ₃ to grow the nozzle inner surface. However, it is difficult to make the inclusions contain SiO ₂ simply by simply increasing the Si concentration, and it is necessary to satisfy at least (wt% Si) / (wt% Ti)> 50. Therefore, the Ti concentration in steel is 0.01
In the case of 0 wt%, in order to obtain a SiO ₂ —Ti oxide, the Si concentration needs to be 0.5 wt% or more. However, an increase in Si causes hardening of the material and also causes deterioration in plating property. An increase in the Si concentration has an adverse effect on the surface properties of the steel sheet, and does not provide a fundamental solution.

Next, in Japanese Patent Publication No. 7-47764, Mn:
Proposal of non-aging cold-rolled steel sheet containing low melting point inclusions consisting of 17-31 wt% MnO-Ti oxide by deoxidizing to 0.03-1.5 wt% and Ti: 0.02-1.5 wt% are doing. In the case of this proposal, since the MnO-Ti oxide has a low melting point and is in a liquid phase in molten steel, the molten steel is injected into the mold without adhering to the nozzle even when passing through the tundish nozzle, Blockage of the tundish nozzle can be effectively prevented. However, as reported by Yasuyuki Morioka, Kazuki Morita et al .: Iron and Steel, 81 (1995), p.
O: In order to obtain a MnO-Ti oxide containing 17 to 31%,
Due to the difference in affinity of Mn and Ti with oxygen, the concentration ratio of Mn and Ti in the molten steel needs to be (wt% Mn) / (wt% Ti)> 100. Therefore, when the Ti concentration in steel is 0.010 wt%,
To obtain the required MnO-Ti oxide, the Mn concentration must be 1.0 wt.
% Or more is required. However, if the Mn content exceeds 1.0 wt%, the material hardens. Therefore, it was practically difficult to form inclusions composed of 17-31 wt% MnO-Ti oxide.

[0010] Further, in Japanese Patent Application Laid-Open No. 8-281394, Al
As prevention of clogging of the tundish nozzle in less Ti-deoxidized steel, by using a material containing CaO · ZrO ₂ grains in the nozzle, if the Ti ₃ O ₅ in the molten steel was trapped in the nozzle, TiO ₂ - A method has been proposed in which a low melting point inclusion of the SiO ₂ —Al ₂ O ₃ —CaO—ZrO ₂ system is used to prevent its growth. However, when the oxygen concentration in the molten steel is high,
Since the TiO ₂ concentration is high and the melting point is not lowered, it does not prevent the nozzle from being clogged. On the other hand, when the oxygen concentration is low, there is a problem that the nozzle is melted, and this is not a sufficient measure.

Further, the above-mentioned prior arts relating to the prevention of nozzle clogging are as follows. In a continuous casting process, an immersion nozzle for injecting molten steel from a tundish nozzle into a mold is still cast by blowing Ar gas or N ₂ gas. There is a need. However, there remains a problem that the blown gas is trapped by the solidified shell of the slab and becomes a cellular defect.

By the way, ultra-low carbon enameled steel sheets are widely used for household appliances such as kitchen appliances, bathtubs, sinks, sanitary appliances, chemical industry products, electric product parts, and building material panels. In particular, in parts where deep drawing formability is required, a high r-value (Rankford value) and an excellent strength-elongation balance are required. It is known that the r value strongly depends on the crystal orientation of the steel sheet, and can be increased by developing {111} recrystallization texture. From this, conventionally, r
In order to increase the value, various studies have been made on the steel composition, hot rolling conditions, cold rolling conditions and annealing conditions as methods for developing {111} recrystallization texture. For example, it is known that when recrystallization annealing is performed at a high temperature, {111} recrystallization texture is strongly developed and the r value is increased. However, in the case of this method, there is a new problem that crystal grains are coarsened due to high-temperature annealing, and the strength-elongation balance required for press formability is rather lowered. In order to ensure excellent press formability, a high strength-elongation balance (TS × El ≧ 15500) is required.

[0013] Further, the enameled steel sheet is indispensably required to have anti-jumping property. In the enamel process, hydrogen that has penetrated into the steel sheet during the enamel manufacturing process aggregates at the interface between the steel sheet and the enamel coating during or immediately after firing and explodes in a circular or semilunar shape. This is a phenomenon that the enamel coating is flipped off. In order to suppress this, in an ordinary enameled steel sheet, inclusions or precipitates are intentionally dispersed in the steel so that hydrogen does not diffuse or coagulate at the interface between the steel sheet and the enamel coating. However, depending on the enamel manufacturer, there are many cases where the steel sheet is manufactured in an environment in which a large amount of hydrogen easily penetrates into the steel beyond the anti-sticking property of the steel sheet. Has not reached the limit.

[0014]

The object of the present invention is to solve the above-mentioned problems of the prior art. A first object of the present invention is to propose a steel sheet for deep drawing enamel having excellent surface properties, formability, and toughness, and a method for producing the same. A second object of the present invention is to propose a technique for producing a steel sheet for deep drawing enamel which is effective for preventing nozzle clogging during continuous casting and effective for preventing generation of cluster-like inclusions. A third object of the present invention is to provide a good surface property and excellent anti-sticking property, and furthermore, TS × El ≧ 15
An object of the present invention is to provide a deep drawn enameled steel sheet having a high strength-elongation balance of 500.

[0015]

Means for Solving the Problems The inventors of the present invention have conducted intensive studies to achieve the above object, and as a result, the size, amount and composition of oxide-based inclusions remaining in steel are within specified ranges. If so, it is possible to finely disperse without causing the above-described nozzle clogging, and without making the inclusions gigantic in a cluster form, and improve the surface properties and the anti-sticking property of the steel sheet, and Is after hot rolling or cold rolling
By controlling the grain growth during annealing, it was found that the strength-elongation balance could be significantly improved, and the present invention was reached.

The present invention developed based on such knowledge,
C ≦ 0.010 wt%, Si ≦ 1.0 wt%, Mn ≦ 3.0 wt%, P ≦ 0.
15 wt%, S ≦ 0.05 wt%, 0.005 wt% ≦ Cu ≦ 1.0 wt%, O
≧ 0.0001wt%, N ≦ 0.02wt%, 0.010wt% ≦ Ti ≦ 0.50wt
%, But 0.005 to 0.2 wt% of this Ti is non-oxide Ti
(Ti ^* ) in the form of Ca and / or metal REM
≧ 0.0005wt%, containing Al in the range satisfying the following formula (1) or (2), with the balance being Fe and unavoidable impurities. This is a steel sheet for deep drawing enamel which is excellent in quality. Note wt% Ti / wt% Al ≧ 5 (1) Al ≦ 0.010 wt%, and wt% Ti / wt% Al <5 ... (2)

The steel sheet of the present invention further comprises, in addition to the above components, Nb: 0.001 to 0.1 wt%, B: 0.0001 to 0.05 wt%,
It is preferable to contain any one or more of Se: 0.0001 to 0.050 wt%. In the present invention,
In each of the above steel sheets, the non-oxide Ti (Ti ^* ) is 0.01 to
0.2 wt% and C (wt%), N (wt%), S
(Wt%), it is preferable that the composition is contained so as to satisfy the following formula: Ti ^* ≧ (4C + 3.4N + 1.5S). It is preferable that each of the steel sheets of the present invention contains 0.002 to 0.015 wt% of oxide inclusions having a size of 50 μm or less. In each of the steel sheets of the present invention, the inclusions in the steel are CaO and / or REM oxide: 5 wt% or more and 50 wt% or less in total, and Ti oxide: 90 wt%.
Hereinafter, it is preferable that Al ₂ O ₃ : mainly contain oxide-based inclusions of 70 wt% or less.

Further, the present invention provides a composition comprising C ≦ 0.
010 wt%, Si ≦ 1.0 wt%, Mn ≦ 3.0 wt%, P ≦ 0.15 wt
%, S ≦ 0.05 wt%, 0.005 wt% ≦ Cu ≦ 1.0 wt%, O ≧ 0.
0001wt%, N ≦ 0.02wt%, 0.010wt% ≦ Ti ≦ 0.50wt%,
However, 0.005 to 0.2 wt% of this Ti is non-oxide Ti (Ti
^* ) In the form of Ca and / or metal REM ≧ 0.
A steel slab containing 0005 wt% and containing Al in a range satisfying the following formula (1) or (2) is heated at 900 to 1300 ° C.
Soak, finish rolling at a temperature of 650 to 960 ° C and finish 400
Winding at a temperature of up to 750 ° C, cold rolling at a reduction of 50 to 95%, and recrystallization annealing at 700 to 920 ° C. We propose a manufacturing method for deep drawing enamels with excellent skipping properties. Note wt% Ti / wt% Al ≧ 5 (1) Al ≦ 0.010 wt%, and wt% Ti / wt% Al <5 ... (2)

In the above method according to the present invention, in addition to the above basic components, the steel slab further contains Nb: 0.001 to 0.1%.
1 wt%, B: 0.0001 to 0.05 wt%, Se: 0.0001 to 0.050 wt
%, It is a preferred embodiment to contain any one or two or more of the above. Further, in each of the above methods of the present invention, the non-oxide Ti (Ti ^* ) is 0.01 to 0.2 wt%, and is related to C (wt%), N (wt%) and S (wt%). In this case, it is preferable to include Ti ^* ≧ (4C + 3.4N + 1.5S) so as to satisfy the following formula: Ti ^* ≧ (4C + 3.4N + 1.5S). In each of the above methods of the present invention, the inclusions in the steel are CaO and / or REM oxide: 5 wt% in total amount.
Above 50 wt% or less, Ti oxides: 90 wt% or less, Al ₂ O _3: 70wt
% Or less of oxide-based inclusions.

[0020]

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS First, an experimental study which will lead to the present invention will be described. In this experiment, C: 0.002 wt%, Si: 0.02 wt%, Mn: 0.1 wt%,
P: 0.01 wt%, S: 0.006 wt%, Al: 0.005 wt%, N:
0.006 wt%, Ti: 0.05-0.15 wt%, O: 0.001-0.020
wt%, Ca: 0.001 wt%, Ti ^* -(4C + 3.4N + 1.5S)
After heating a sheet bar having a composition of 0.04 (Ti ^* : non-oxide Ti) to 1100 ° C. and soaking, the finishing temperature is 9
Three-pass rolling was performed at 20 ° C. to obtain a 3.2 mm-thick hot-rolled sheet. Thereafter, coil winding was performed at 650 ° C. for 1 hour. Then, after cold rolling of 80%, recrystallization annealing at 880 ° C. for 40 seconds was performed.

FIG. 1 shows the effect of the amount of oxides on the tendency of occurrence of jumps and TS × EL in the formability of the steel sheet manufactured as described above. Here, the tendency of occurrence of skipping was determined by pickling the annealed plate at 75 ° C. in a 10% aqueous sulfuric acid solution for 20 seconds, applying a commercial undercoat glaze to a thickness of 100 μm, and then increasing the dew point by +40. After baking for 1 minute in a baking furnace at 800 ° C. and a heating temperature of 800 ° C., the film was inserted into a constant temperature bath at 160 ° C. for 10 hours, and the number of toes generated on the enamel coating was evaluated. In addition, as for this steel plate, as a result of observing the vicinity of the steel plate surface with a microscope, the size of the oxide-based inclusions of the steel plate was 50 μm or less in the width direction of the steel plate. As is clear from this figure, in the steel sheet of this component composition, the number of occurrences of jumps and TS × EL depend on the amount of oxide, and when the amount of oxides is 0.002 to 0.015 wt%, the occurrence of jumps does not occur. And good TS × EL was obtained, especially when the oxide amount was 0.004 to 0.012
When wt%, it was found that the toe skipping resistance and TS × EL characteristics were even better.

(1) Steel composition The composition of the steel sheet according to the present invention is as follows: C ≦ 0.010 wt%, Si ≦ 1.0 wt%, Mn ≦ 3.0 wt%, P
≦ 0.15wt%, S ≦ 0.05wt%, 0.005wt% ≦ Cu ≦ 1.0wt
%, O ≧ 0.0001wt%, N ≦ 0.02wt%, 0.010wt% ≦ Ti ≦
0.50 wt%, containing Ca and / or metal REM ≧ 0.0005 wt%, and wt% Ti / wt% Al ≧ 5, or Al ≦ 0.01
0 wt% and wt% Ti / wt% Al <5
And 0.005 to 0.2 wt% of non-oxide Ti
(Ti ^* ), and the non-oxide Ti (Ti ^* ) is 0.01 to 0.2 wt.
% And C (wt%), N (wt%), S (wt%)
In relation to the following formula: Ti ^* ≧ (4C + 3.4N + 1.5S), and further, if necessary, Nb: 0.001 to 0.1 wt.
%, B: 0.0001 to 0.05 wt%, Se: 0.0001 to 0.050 wt%, and the balance is Fe and inevitable impurities.

Hereinafter, the component composition of the steel sheet according to the present invention will be described.
The reason for limiting as described above will be described. (a) C ≦ 0.010 wt% It is preferable to reduce the content of C as the smaller the content, the better the deep drawability is improved. However, considering the refining load and the like, the upper limit is set to 0.010 wt% or less without adverse effects. (b) Si ≦ 1.0 wt% Si has the effect of strengthening steel, and contains the necessary amount according to the desired strength. However, if the content exceeds 1.0 wt%, deep drawability deteriorates. It was limited to 1.0 wt% or less. (c) Mn ≦ 3.0 wt% Mn has the effect of strengthening steel and contains the necessary amount according to the desired strength. However, if the content exceeds 3.0 wt%, deep drawability deteriorates. It was limited to 3.0 wt% or less. (d) P ≦ 0.15wt% P has the effect of strengthening steel and contains a necessary amount according to the desired strength. However, if the content exceeds 0.15wt%, deep drawability deteriorates. Limited to 0.15 wt% or less. (e) S ≦ 0.05 wt% It is preferable to reduce the content of S because the smaller the content, the better the deep drawability. However, if the content is 0.05 wt% or less,
Since there is no significant adverse effect, the content was limited to 0.05 wt% or less. (f) 0.005 wt% ≦ Cu ≦ 1.0 wt% Cu is an element that increases the surface roughness of the steel sheet when pickling the steel sheet as a pretreatment for enamel processing and improves the adhesion of the enamel coating. To exert such an effect, 0.005 wt% or more is required. However, if it exceeds 1.0 wt%, the pickling speed is reduced and the surface roughness of the steel sheet is lost. Therefore, the added amount of Cu is 0.005 to 1.
The range is 0 wt%. The preferred range is 0.02 to 0.10
wt%. (g) O ≧ 0.0001 wt% O is a useful element that forms inclusions that improve the anti-sticking property. Such an effect can be obtained by adding 0.0001% by weight or more. However, if it is contained in a large amount, it may cause surface defects. Therefore, it is preferable to add 0.10 wt% as an upper limit. (h) N ≦ 0.02 wt% It is preferable to reduce the N content because the smaller the content, the better the deep drawability. However, if the content is 0.02 wt% or less,
Since there is no significant adverse effect, the content was limited to 0.02 wt% or less. (i) 0.010 wt% ≦ Ti ≦ 0.50 wt% Ti is a component that plays the most important role in the steel sheet of the present invention, and forms fine oxide-based inclusions having a size of 50 μm or less by Ti deoxidation. A component that controls the grain growth during cold rolling and annealing to improve the balance between strength and elongation. Further, since this fine oxide effectively acts on miniaturization of a hot-rolled sheet, it develops {111} recrystallized texture after cold rolling and annealing to increase the r-value. If the Ti content is less than 0.010 wt%, the effect of addition, that is, the amount of the fine oxide is too small, so that the desired effect described above cannot be obtained.
The lower limit was limited to 0.010 wt% or more. This Ti is 0.025 wt
% More effective when added. However, 0.50wt%
If added in excess of the above, the material of the thin steel sheet is hardened, not only impairing the desired material properties, but also increasing the cost. Therefore, the upper limit is set to 0.50 wt%.

(J) Al Al is a component that plays an important role in the present invention, and is represented by wt% Ti / wt% Al ≧ 5 or Al ≦ 0.010 wt%
In addition, it is necessary to satisfy one of the conditions of wt% Ti / wt% Al <5. When the above conditions are no longer satisfied, it becomes Al deoxidized steel, a large amount of Al ₂ O ₃ clusters are generated, and the surface properties of the steel slab are deteriorated, and the grain growth during cold rolling-annealing is controlled. Therefore, the amount of fine oxide of 50 μm or less is reduced, and the strength-elongation balance is inferior. Therefore, it is necessary that the Al content satisfies the above conditions or the above conditions, and the above conditions are particularly preferable ranges for achieving the object of the present invention.

(K) Ca and / or metal REM ≧ 0.0005
The wt% Ca and the metal REM are components that play an important role in the steel sheet according to the present invention, and it is necessary to add one or two of Ca and REM in a total of 0.0005 wt% or more. That is, after deoxidizing molten steel with Ti, one or two of Ca and REM are further added in a total amount of 0.0005 wt%.
By adding the above, the oxide composition in the molten steel is adjusted to Ti oxide: 90 wt% or less, preferably 20 wt% or more and 90 wt% or less,
More preferably 85% by weight or less, CaO and / or RE
M oxide: 5 wt% or more, preferably 8 wt% to 50 wt%, and adjusted so as to be low melting point oxide-based inclusions in which Al ₂ O ₃ is 70 wt% or less. By performing such an adjustment, it is possible to prevent the Ti oxide containing the base metal from adhering to the nozzle during continuous casting, thereby eliminating nozzle blockage. further,
CaO and / or REM oxide can contribute to grain growth after cold rolling and annealing and grain refinement of a hot rolled sheet. Note that excessive
Since the addition of Ca and REM can cause rust,
It is desirable to add in a total amount of 0.005 wt% or less.

(L) Non-oxide Ti (Ti ^* ) = 0.005-0.2 wt
% Ti ^* ≧ (4C + 3.4N + 1.5S) Non-oxide Ti refers to Ti that does not exist in an oxide state in steel among all Ti, that is, exists as a carbide, nitride, sulfide, or a solid solution state Means the total amount of Ti present and is determined by the following method. Non-oxide Ti content = total Ti content−oxide Ti Here, oxide Ti = total O content × Ti concentration of inclusions in steel by EPMA (wt%) / O concentration of inclusions in steel by EPMA (wt%) ). And the Ti concentration and the O concentration by EPMA are selected from 10 oxide inclusions of 3 to 10 μm randomly present in the steel, and the concentration is measured by EPMA.
Use the average value. The non-oxide Ti obtained in this way is a component that plays a very important role in the steel sheet according to the present invention, and converts solid solution C, solid solution N, and solid solution S in the steel as carbide, nitride, and sulfide. By reducing the precipitation and fixing, there is an effect of preventing the deterioration of the deep drawability. The amount
If the content is less than 0.005 wt%, there is no effect, and if it exceeds 0.2 wt%, no further effect is obtained, and conversely, deep drawability is deteriorated. Note that the content of Ti ^* is desirably 0.01 wt% or more. And
The amount of the non-oxide Ti (Ti ^* ) must satisfy the relational expression of Ti ^* ≧ (4C + 3.4N + 1.5S) in relation to the respective contents of C, N, and S. Because Ti ^* <(4
(C + 3.4N + 1.5S), since a large amount of solid solution C remains in the hot-rolled sheet, the deep drawability after cold rolling and annealing is inferior.

(M) Nb: 0.001 to 0.1 wt% Nb has the effect of improving the r-value after cold rolling and annealing by making the structure of the hot-rolled sheet finer. The addition amount is 0.00
If it is less than 1 wt%, there is no effect of addition, while if it exceeds 0.1 wt%, the effect of the addition is saturated and conversely leads to deterioration of deep drawability, so it was limited to the range of 0.001 to 0.1 wt%. (n) B: 0.0001 to 0.05 wt% B is added for improving the resistance to secondary working brittleness of steel. However, if the addition amount is less than 0.0001 wt%, there is no addition effect.
On the other hand, if added in excess of 0.05 wt%, it will lead to deterioration of the deep drawability, so it was limited to 0.0001 to 0.05 wt%. (o) Se: 0.0001 to 0.050 wt% Se is an element that improves the flowability (surface tension) of the molten metal during welding, and 0.0001 wt% or more is added as necessary. But,
If it is added in excess of 0.050 wt%, the pickling rate is reduced, and the surface roughness of the steel sheet is lost. Therefore, 0.0001-0.
Add in the range of 050 wt%. The preferred range is 0.00
30 to 0.030 wt%.

(2) Inclusion of Slab and Steel Sheet For the steel sheet of the present invention, the width direction of the steel sheet (direction perpendicular to the rolling direction)
It is necessary to adjust so as to contain 0.002 to 0.015 wt% of fine oxide inclusions having a size of 50 μm or less. By the way, the size of the inclusions present in the slab (slab) is elongated in the rolling direction by rolling, but hardly changes in the plate width direction. Therefore, in order to keep the size of the inclusion in the width direction of the steel sheet within a predetermined range, it is necessary to control the size of the inclusion at the stage of the billet. For this reason,
Control of fine oxide-based inclusions contained in a billet is one of the important components of the present invention. In particular, the inclusions produced under the method of the invention have a width (dimension in the direction perpendicular to the rolling) of 50 μm.
It is a granular or fractured oxide-based inclusion having the following size. If the oxide inclusions have a width of 50 μm or less,
It is possible to suppress crystal grain refinement during hot rolling and grain growth during cold rolling and annealing. However, inclusions having a width larger than 50 μm do not have the above-described effect. For this reason, the oxide inclusions were limited to those having a width of 50 μm or less.
When the content of the oxide-based inclusions is less than 0.002 wt%, it has no effect on the toughness and control of grain growth. On the other hand, when the content of the oxide-based inclusions exceeds 0.015 wt%, the deep drawability is adversely affected. Since it deteriorates, the content is limited to 0.002 to 0.015 wt%. From the viewpoint of deep drawability, the content of oxide-based inclusions is preferably 0.004 to 0.012 wt%. Where the width is 50μ
Granular or fractured oxide inclusions with a size of less than m are oxide inclusions formed from steel slabs, and relatively large ones are cut in the rolling direction by hot rolling and cold rolling. A fractured oxide-based inclusion that has been broken is referred to, and a relatively small one is a particulate oxide-based inclusion that maintains its shape.

(3) Steel Sheet Manufacturing Method Steelmaking Step: This step is not particularly limited in the case of the present invention, but preferred processing methods are exemplified below.
The material is ultra-low carbon steel, Ti ≧ 0.010 wt%,
wt% Ti / wt% Al ≧ 5 or Al ≦ 0.010 wt% and wt
% Ti / wt% Al <5 It is necessary to melt a steel having a component composition that satisfies either condition. In this case, the reason for making Ti ≧ 0.010 wt% as the adjusting component is Ti <
At 0.010 wt%, the deoxidizing ability is weak, the total oxygen concentration in the molten steel increases, and the material properties such as elongation and drawing are deteriorated. However, even in this case, it is conceivable that the deoxidizing power is increased by increasing the concentration of Si and Mn. However, when Ti <0.010 wt%, a large amount of inclusions containing SiO ₂ or MnO is generated, and the hardening of the steel material and The enamel surface quality is degraded. To prevent this, (wt% Ti) / (wt% Al) ≧ 5, (wt% Mn) / (wt% Ti)
<100, in which case the Ti in the inclusions
The oxide concentration is above 20%.

Also, wt% Ti / wt% Al ≧ 5, or
The reason for setting any of the conditions of Al ≦ 0.010 wt% and wt% Ti / wt% Al <5 is that if these conditions are not satisfied, Ti
This is because Al deoxidized steel is used instead of deoxidized steel, and a large amount of Al ₂ O ₃ clusters having an Al ₂ O ₃ concentration of 70% or more are generated. The present invention is intended to achieve the intended purpose by including CaO and REM oxide in inclusions mainly composed of Ti oxide as described later. In this regard, it is preferable that the above two conditions be adjusted particularly to the condition of wt% Ti / wt% Al ≧ 5.

In manufacturing the steel sheet according to the present invention,
First, molten steel is deoxidized with a Ti-containing alloy such as Fe-Ti to generate oxide-based inclusions mainly composed of Ti oxides in the steel.
The inclusions are not in the form of huge clusters as in the case of deoxidation with Al, but mostly in the form of granules or fractures having a size of about 1 to 50 μm. However, at this time, if the above or the above conditions are not satisfied, a huge Al ₂ O ₃ cluster is generated. Such Al ₂ O ₃ clusters can be obtained by adding Ti alloy.
Even if the Ti concentration is increased, it cannot be reduced and remains as cluster-like inclusions in the steel. Therefore, in the steel sheet according to the present invention, at this stage of production, first, an appropriate Ti
Preferably, an oxide is formed.

Under the method of the present invention, the yield of Ti alloy is lower than that of the conventional method of deoxidizing with Al,
a, Inclusion composition adjusting alloys are expensive because they contain REM. For this reason, it is economically preferable to add the Ti alloy to the molten steel so that the addition of the Ti alloy is as small as possible within a range where the composition of the inclusions can be controlled. In this sense, prior to the addition of a deoxidizing material such as a Ti-containing alloy, it is desirable to carry out preliminary deoxidation in order to reduce dissolved oxygen in the molten steel and FeO and MnO in the slab. This preliminary deoxidation is performed by deoxidation with a small amount of Al such that Al ≦ 0.010 wt% in the molten steel after deoxidation, and addition of Si, FeSi, Mn, and FeMn.

As described above, Ti produced by Ti deoxidation
A steel sheet with Ti oxide-based inclusions of ₂ O ₃ ≧ 70% means that the inclusions are dispersed in the steel with a size of about 2 to 20 μm. Disappears. However, Ti oxide is in a solid state in molten steel, and ultra-low carbon steel grows on the inner surface of a tundish nozzle with metal incorporation due to the high solidification temperature of the steel. May be induced.

Therefore, in the present invention, after deoxidation with a Ti alloy, one or more of Ca and REM are further added so as to be 0.0005 wt% or more, and the molten steel, and thus the steel Oxide composition, Ti oxide: 20 wt% or more 90
wt% or less, preferably 85 wt% or less, CaO and / or R
EM oxide: a low melting point oxide-based inclusion containing 5 wt% or more, preferably 8 wt% or more and 50 wt% or less, and Al ₂ O ₃ of 70 wt% or less. Then, it becomes possible to effectively prevent the Ti oxide incorporating the metal from adhering to the nozzle. In addition,
A more desirable inclusion composition is Ti ₂ O ₃ : 30 wt% or more and 80 wt%
% Or less, CaO, REM oxide (La ₂ O ₃ , Ce ₂ O ₃ etc.): 10
It is not less than wt% and not more than 40 wt%. 20 Ti oxides of the above inclusions
If it is less than wt%, it will not be Ti deoxidized steel but Al deoxidized steel, and Al ₂ O
Nozzle clogging because the growing ₃ concentration is generated, also, Ca
Since the rusting deteriorates as the O, REM oxide concentration increases, the Ti oxide concentration is set to 20 wt% or more. On the other hand, when the Ti oxide concentration is 90 wt% or more, CaO and REM oxides are small and nozzle clogging occurs, so that the Ti oxide concentration is 20 wt% or more and 90 wt% or more.
wt% or less.

Further, regarding Al ₂ O ₃ in the inclusions,
If the content exceeds 70 wt%, the composition will have a high melting point, and not only will the nozzle be blocked, but the inclusions will also form clusters, which will increase nonmetallic inclusion defects on the product plate.

As described above, the oxide-based inclusions in the steel according to the present invention include CaO and / or REM oxide in a total amount of 5 wt% to 50 wt%, Ti oxide in a total amount of 90 wt% or less, and Al ₂ O ₃ Ti oxide containing less 70 wt% of the need as the main. The oxide-based inclusions may further include oxides such as SiO ₂ and MnO in addition to the oxides. In this case, it is desirable to control the content of SiO ₂ in the inclusions to 30 wt% or less and the content of MnO to 15 wt% or less. The reason is that if these contents exceed the respective amounts, it cannot be said that the titanium-killed steel is the target of the present invention.Under such a composition, there is no nozzle clogging without Ca addition, and there is no problem of rusting. It is because it disappears. Moreover,
As described above, in order to include SiO ₂ and MnO in the inclusions, the Si and Mn concentrations of the molten steel are set to Mn / Ti> 100 and Si / Ti> 50.
Is preferable. In addition, the oxide of the present invention is allowed to contain ZrO ₂ , MgO and the like in a range of 5 wt% or less. Incidentally, the composition of the oxide-based inclusions in the steel described above, arbitrarily extract ten oxide-based inclusions,
It is determined from the average value (analytical value).

In the steel sheet according to the present invention, the conventional Al
Compared to deoxidized steel, the yield of Ti alloy is poor, and Ca, REM
Is expensive due to the addition of For this reason, it is preferable to adjust the composition of inclusions in steel so that the amount is as small as possible.If possible, pre-deoxidize so that the dissolved oxygen concentration in the molten steel before Ti deoxidation becomes 200 ppm or less. Is desirable. This preliminary deoxidation is preferably performed by stirring the molten steel in a vacuum, deoxidizing with a small amount of Al (Al after deoxidation is 0.010 wt% or less in the molten steel), and deoxidizing with Si, FeSi, Mn, or FeMn.

The size of the inclusion controlled as described above has a size of 50 μm or less. here,
The reason for limiting the size of inclusions to those of 50 μm or less is as follows:
In the deoxidation method according to the present invention, inclusions of 50 μm or more are hardly generated. This is because the inclusions having a size of 50 μm or more are generally caused by foreign inclusions such as slag and mold powder. It is desirable that the amount of inclusions of 50 μm or less be present in an amount of 80 wt% or more of the total amount of the oxide-based inclusions in order to prevent coil surface defects and nozzle clogging.

In the present invention, when the composition of the formed inclusions is controlled as described above, it is possible to completely prevent oxides and the like from adhering to the inner surfaces of the tundish nozzle and the immersion nozzle of the mold during continuous casting. . Therefore, it is not necessary to blow a gas such as Ar or N ₂ into the tundish or the immersion nozzle for preventing adhesion of oxides and the like. As a result, it is possible to obtain an effect that it is possible to prevent powdery defects of the cast slab due to powder entrainment during continuous casting and bubble-like defects due to the blown gas from being generated in the cast slab.

Hot rolling step: The slab is heated at a temperature of 900 to 1300 ° C. prior to the hot rolling. The reason for this is that at a slab heating temperature of 900 ° C. or less, the load applied during rolling becomes too high, which causes operational problems. On the other hand, 1300
At a high temperature exceeding ℃, the crystal grain size before rolling becomes too large, so that the hot-rolled sheet does not become fine. Therefore, the slab heating temperature is limited to 900 to 1300 ° C. The slab heating temperature is preferably 1200 ° C. or less from the viewpoint of deep drawing. In the process from continuous casting to rolling, CC-DR (continuous casting-direct rolling) or
Adopting HCR (hot charge rolling) is a preferable method from the viewpoint of energy saving.

The end temperature of the hot rolling is 650 to 960 ° C.
And The reason is that when hot rolling is completed at a temperature higher than 960 ° C., the crystal grains of the hot-rolled sheet are coarsened, and the deep drawability after cold rolling and annealing is deteriorated. On the other hand, hot rolling may be terminated in the α region below the Ar ₃ transformation point, but if the temperature is lower than 650 ° C., the rolling load increases, so the finish rolling end temperature is set to 650 to 960 ° C. limit. As for the coil winding temperature after hot rolling, higher temperatures are more advantageous for coarsening of precipitates.However, if the temperature exceeds 750 ° C, the scale becomes too thick. Is not coarsened, so it is limited to the range of 400 to 750 ° C.

Cold rolling step: This step is a process performed to obtain a high r value, and in order to achieve this purpose, it is necessary to set the cold rolling reduction to 50 to 95%. This is because if the rolling reduction is less than 50%, excellent deep drawability cannot be obtained. On the other hand, even if cold rolling is performed at a rolling reduction of 95% or more, a higher r value is obtained. Is not obtained, and conversely, the r-value is reduced, so that it is limited to 50 to 95%.

Annealing step: The cold-rolled steel sheet that has undergone the cold rolling step must be subjected to recrystallization annealing. Annealing temperature is 700 ~ 92
Set to 0 ° C. This is because if the annealing temperature is below 700 ° C,
The preferred {111} recrystallization texture for deep drawability does not develop.On the other hand, even if annealing is performed in a high temperature region exceeding 920 ° C, further deep drawability cannot be obtained. This is because the texture is randomized and the r value is degraded. Therefore, the annealing temperature is limited to 700-920 ° C. The steel strip after annealing may be subjected to a temper rolling of 10% or less for shape correction, adjustment of surface roughness, and the like.

The hot-rolled steel sheet or cold-rolled steel sheet thus obtained can be used not only as a steel sheet for processing but also as an original sheet of a surface-treated steel sheet for processing. Examples of the surface treatment include zinc plating (including alloys), tin plating, and resin coating. In addition, the steel sheet of the present invention is subjected to a special treatment after annealing or galvanizing, so that
The weldability, press formability, corrosion resistance and the like may be improved.

[0045]

EXAMPLES Example: After tapping the converter, 300 ton of molten steel was decarburized using an RH degassing apparatus, and C: 0.0012 to 0.0062 wt%, S
i: 0.007 to 0.022 wt%, Mn: 0.10 to 0.29 wt%, P: 0.0
06 to 0.012 wt%, S: 0.0015 to 0.033 wt%, Cu: 0.03 to
Adjust to 0.08wt% and raise the temperature of molten steel to 1575 ~ 1610 ℃
Was adjusted. Al was added to the molten steel in an amount of 0.2 to 0.8 kg / ton to reduce the dissolved oxygen concentration in the molten steel to 50 to 300 ppm. At this time, the Al concentration in the molten steel was 0.001 to 0.006 wt%. Then, 70wt% Ti-Fe alloy is added to this molten steel in the range of 0.8 to 1.
8 kg / ton was added to deoxidize Ti. Then, after adjusting the composition by adding FeNb, FeB, etc., 30 wt% Ca-
60wt% Si alloy and Met.Ca, Fe, 5 ~ 15wt% RE
M-mixed additive, or Ca alloy such as 90wt% Ca-5wt% Ni alloy, REM alloy Fe-coated wire is 0.05-0.5
kg / ton was added for treatment. The Ti concentration after this treatment
0.068 to 0.120 wt%, Al concentration 0.001 to 0.004 wt%, Ca
Concentration is 0.0024-0.0095wt%, REM concentration is 0.0000-0.00
30 wt%.

Next, this molten steel was continuously used for two strand slabs.
The cast slab was manufactured by casting using a casting apparatus. Note that this
Average structure of molten steel inclusions in a tundish
Is 25-85wt% Ti_TwoO_Three− 5 to 45 wt% CaO − 0 to 18 wt% R
EM oxide-6 ~ 41wt% Al_TwoO _ThreeFine spherical inclusions
Was. During this casting, tundish and immersion
Ar gas was not blown into the fuel cell. Observe after continuous casting
In a tundish and immersion nozzle
Had almost no deposits.

Next, the continuous cast slab is hot-rolled, cold-rolled to 0.8 mm, and further subjected to a continuous annealing line (C
AL) or recrystallization annealing was performed in a hot-dip galvanizing line (CGL). Table 1 shows the steel composition, the content of oxide inclusions with a dimension of 50 μm or less in the sheet width direction, the composition of the inclusions (average composition of the inclusions in the main steel sheet of 1 μm or more), and the surface properties of the coil. It is shown in FIG. Table 3 shows the conditions of hot rolling, cold rolling and annealing. The obtained steel sheet was examined for mechanical properties, anti-jumping property, and the like. The tendency of occurrence of toe jumping is as follows.
Pickling in a 10% sulfuric acid aqueous solution for 20 seconds, glazing a commercial undercoat glaze to a thickness of 100 μm, and then dew point +
After firing for 1 minute in a firing furnace at 40 ° C and a heating temperature of 800 ° C,
It was inserted into a thermostat at 160 ° C for 10 hours, and evaluated by the number of jumps generated in the enamel coating. The non-oxide Ti, mechanical properties, and the like in Tables 2 and 3 were determined in the same manner as described above. Non-metallic inclusion defects such as barbs, slivers, scales, etc. were found in this annealed plate at 0.00 to 0.02 / 1000 m-coil or less. In addition, the amount of rusting
As with deoxidation, there was no problem. The surface quality of the steel sheet subjected to the electroplating and the hot-dip galvanizing treatment after the cold rolling was also good. Table 3 summarizes the mechanical properties, the toe skipping resistance, and the like of the steel sheet. As shown in Tables 1 to 3, all of the examples of the invention had good surface properties and strength-elongation balance, and also had excellent skipping resistance.

[0048]

[Table 1]

[0049]

[Table 2]

[0050]

[Table 3]

Comparative example: After tapping from the converter, 300 ton of molten steel was RH
Decarburized by degassing equipment, C: 0.0015-0.0042wt%,
Si: 0.007 to 0.035 wt%, Mn: 0.08 to 0.23 wt%, P: 0.
007 to 0.009 wt%, S: 0.015 to 0.022 wt%, Cu: 0.0
Adjust to 3 to 0.04 wt% and raise the molten steel temperature to 1589 to 160
Adjusted to 0 ° C. 1.2-1.6 kg / ton of Al
It was added and deoxidized. The Al concentration in the molten steel after the deoxidation treatment was 0.035 to 0.051 wt%. Then, while adding Fe-Ti, Fe-Nb and Fe-B were added to adjust the component composition. The Ti concentration after this treatment was 0.001 to 0.
011 wt%. Next, the molten steel was cast by a two-strand slab continuous casting apparatus to produce a continuously cast slab.
Incidentally, in this case, the average composition of inclusions contained in the tundish molten steel, cluster-like inclusions consisting _{95~98wt% Al 2 O 3, 5wt} % or less of Ti ₂ O ₃ is in principal there were. Ar in the tundish and immersion nozzle during casting
If no gas was blown, Al ₂ O
_At the third charge, the opening of the sliding nozzle was significantly increased, and the casting was stopped due to nozzle clogging. Also, when Ar gas is blown, Al ₂ O
₃ was attached in a large amount, and at the 8th charge, the fluctuation of the molten metal level in the mold became large and the casting was stopped. Next, the continuous cast slab was hot-rolled to 3.2 mm, cold-rolled to 0.8 mm, and further subjected to recrystallization annealing in a continuous annealing line. Table 1 shows the steel composition and Table 2 shows the inclusion composition.
Table 3 shows the respective conditions (manufacturing conditions) of hot rolling, cold rolling and annealing. The surface properties, mechanical properties, and anti-sticking properties are shown in Table 3 as comparative examples. Non-metallic inclusion defects such as barbs, slivers and scales were found in these annealed sheets at 0.48 to 0.58 / 1000 m-coil. In addition, the TS × El balance was inferior to that of the invention example, and jumping occurred.

[0052]

As described above, the ultra-low carbon steel sheet according to the present invention does not cause clogging of the immersion nozzle at the time of continuous casting in the production thereof, and the surface of the rolled thin steel sheet has nonmetallic inclusions. This is a very clean deep drawn enameled steel sheet with almost no surface defects caused by the above. Further, it has a good balance between toe jumping resistance and excellent strength and elongation, so that it is actually suitably used for deep drawing enamel. Further, this steel sheet can be used as a steel sheet for automobiles and other surface-treated steel sheets without any problem.

[Brief description of the drawings]

FIG. 1 is a graph showing the effect of the amount of fine oxide inclusions on the number of jumps and TS × EL.

 ────────────────────────────────────────────────── ─── Continuing from the front page (72) Osamu Furukun, Inventor: 1 Kawasaki-cho, Chuo-ku, Chiba-shi, Chiba Pref. Kawasaki Steel Engineering Co., Ltd. No address) Inside Mizushima Works of Kawasaki Steel Corporation (72) Inventor Taro Yahiro 1-chome, Mizushima Kawasaki-dori, Kurashiki-shi, Okayama Prefecture 1-chome, Kawasaki-dori, Mizushima, Ichikawa (without address) F-term (reference) 4K037 EA02 EA04 EA09 EA13 EA15 EA16 EA18 EA19 EA22 EA23 EA25 EA27 EA31 EA36 EB02 EB03 FC03 FA03 FE02 FE03 FJ05 FJ06 HA05

Claims (9)

[Claims] 1. C ≦ 0.010 wt%, Si ≦ 1.0 wt%, Mn ≦ 3.
0 wt%, P ≦ 0.15wt%, S ≦ 0.05wt%, 0.005wt% ≦ Cu
≦ 1.0 wt%, O ≧ 0.0001 wt%, N ≦ 0.02 wt%, 0.010 wt
% ≦ Ti ≦ 0.50wt%, of which 0.005 to 0.2wt%
% Is contained in the form of non-oxide Ti (Ti ^* ), contains Ca and / or metal REM ≧ 0.0005 wt%, and has the following (1)
A deep-drawn enameled steel sheet having good surface properties and excellent toughness, characterized by containing Al in a range satisfying the formula or the formula (2), the balance being Fe and unavoidable impurities. Note wt% Ti / wt% Al ≧ 5 (1) Al ≦ 0.010 wt%, and wt% Ti / wt% Al <5 ... (2) 2. The steel sheet according to claim 1, further comprising Nb: 0.001 to 0.1 wt%, B: 0.0001 to
A deep drawn enameled steel sheet having good surface properties and excellent toe-jumping resistance, characterized by containing one or more of 0.05 wt% and Se: 0.0001 to 0.050 wt%. 3. The steel sheet according to claim 1, wherein the non-oxide Ti (Ti ^* ) is 0.01 to 0.2 wt%,
And a surface characterized by containing Ti ^* ≧ (4C + 3.4N + 1.5S) in relation to C (wt%), N (wt%), and S (wt%). A deep drawing enameled steel sheet that has good properties and excellent toughness. 4. The steel sheet according to claim 1, 2 or 3, wherein oxide-based inclusions having a size of 50 μm or less are contained in an amount of 0.002 to 0.002 μm.
A deep drawn enameled steel sheet with good surface properties and excellent anti-sticking properties, characterized by containing 0.015 wt%. 5. The steel sheet according to claim 1, wherein the inclusions in the steel are CaO and / or REM oxide: at least 5 wt% in total.
For deep drawing enamels with good surface properties and excellent anti-sticking properties, mainly containing oxide inclusions of 50 wt% or less, Ti oxide: 90 wt% or less, Al ₂ O ₃ : 70 wt% or less steel sheet. 6. As a basic component, C ≦ 0.010 wt%, Si ≦
1.0 wt%, Mn ≦ 3.0wt%, P ≦ 0.15wt%, S ≦ 0.05wt
%, 0.005 wt% ≦ Cu ≦ 1.0 wt%, O ≧ 0.0001 wt%, N ≦
0.02 wt%, 0.010 wt% ≦ Ti ≦ 0.50 wt%, wherein 0.005 to 0.2 wt% of the Ti is contained in the form of non-oxide Ti (Ti ^* ), and Ca and / or metal REM ≧ 0.0005 wt%. A steel slab containing Al in a range satisfying the following formula (1) or (2) is heated and soaked at 900 to 1300 ° C.
Finish rolling at a temperature of 960 ° C, winding at a temperature of 400 to 750 ° C, then cold rolling at a reduction of 50 to 95%, and then recrystallization annealing at 700 to 920 ° C A method for producing a steel sheet for deep drawing enamel having good surface properties and excellent anti-jumping property. Note wt% Ti / wt% Al ≧ 5 (1) Al ≦ 0.010 wt%, and wt% Ti / wt% Al <5 ... (2) 7. The method according to claim 6, wherein the slab further comprises Nb: 0.001 to 0.1 wt% in addition to the above basic components.
Manufacture of steel sheet for deep drawing enamel having good surface properties and excellent toe jumping resistance, characterized by containing one or more of B: 0.0001 to 0.05 wt% and Se: 0.0001 to 0.050 wt%. Method. 8. The method according to claim 6, wherein the non-oxide Ti (Ti ^* ) is 0.01 to 0.2 wt%,
And a surface characterized by containing Ti ^* ≧ (4C + 3.4N + 1.5S) in relation to C (wt%), N (wt%), and S (wt%). A method for producing a steel sheet for deep drawing enamel, which has good properties and excellent toughness. 9. The method according to claim 6, wherein the inclusions in the steel are CaO and / or REM oxide: 5 wt% or more in total.
50 wt% or less, Ti oxides: 90 wt% or less, Al ₂ O _3: 70wt% or less, characterized in that it comprises mainly of oxide inclusions, deep surface properties excellent good resistance to Tsumatobi resistance wandering Manufacturing method for steel sheet.