EP1920078B1 - Steel sheet for deep drawing having excellent secondary work embrittlement resistance, fatigue properties and plating properties, and method for manufacturing the same - Google Patents
Steel sheet for deep drawing having excellent secondary work embrittlement resistance, fatigue properties and plating properties, and method for manufacturing the same Download PDFInfo
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- EP1920078B1 EP1920078B1 EP06769200A EP06769200A EP1920078B1 EP 1920078 B1 EP1920078 B1 EP 1920078B1 EP 06769200 A EP06769200 A EP 06769200A EP 06769200 A EP06769200 A EP 06769200A EP 1920078 B1 EP1920078 B1 EP 1920078B1
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 124
- 239000010959 steel Substances 0.000 title claims abstract description 124
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 19
- 238000000034 method Methods 0.000 title claims abstract description 16
- 238000007747 plating Methods 0.000 title claims description 38
- 239000000203 mixture Substances 0.000 claims abstract description 17
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 15
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 15
- 239000012535 impurity Substances 0.000 claims abstract description 8
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 8
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 8
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 8
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 6
- 239000002244 precipitate Substances 0.000 claims description 32
- 238000005096 rolling process Methods 0.000 claims description 28
- 238000000137 annealing Methods 0.000 claims description 14
- 238000005098 hot rolling Methods 0.000 claims description 11
- 238000005097 cold rolling Methods 0.000 claims description 7
- 239000010960 cold rolled steel Substances 0.000 claims description 6
- 239000002131 composite material Substances 0.000 claims description 6
- 238000003303 reheating Methods 0.000 claims description 6
- 239000006104 solid solution Substances 0.000 description 13
- 230000006866 deterioration Effects 0.000 description 11
- 230000015572 biosynthetic process Effects 0.000 description 10
- 238000000227 grinding Methods 0.000 description 9
- 230000001965 increasing effect Effects 0.000 description 8
- 230000000694 effects Effects 0.000 description 7
- 230000002708 enhancing effect Effects 0.000 description 7
- 238000005728 strengthening Methods 0.000 description 7
- 150000004767 nitrides Chemical class 0.000 description 6
- 239000000047 product Substances 0.000 description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 3
- 238000007792 addition Methods 0.000 description 3
- 238000009826 distribution Methods 0.000 description 3
- 230000001747 exhibiting effect Effects 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 101710178035 Chorismate synthase 2 Proteins 0.000 description 2
- 101710152694 Cysteine synthase 2 Proteins 0.000 description 2
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 2
- 230000032683 aging Effects 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 230000003247 decreasing effect Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 230000002542 deteriorative effect Effects 0.000 description 2
- 239000012467 final product Substances 0.000 description 2
- 238000005244 galvannealing Methods 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- 230000003213 activating effect Effects 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 230000002000 scavenging effect Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
Classifications
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- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
-
- 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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—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
-
- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
Definitions
- the present invention is based on, and claims priority from, Korean Application Number 2005-61691, filed July 8, 2005 , the disclosure of which is incorporated by reference herein in its entirety.
- the present invention relates to steel sheets for deep drawing mainly used for interior or exterior plates of automobile bodies, and the like. More particularly, the present invention relates to steel sheets for deep drawing, which have a tensile strength of 28 - 50 ⁇ f/ ⁇ while exhibiting excellent secondary work embrittlement resistance, fatigue properties of welded joints, and plating properties as well as excellent formability, and to a method for manufacturing the same.
- steel sheets for the automobile body have been required to have further enhanced formability.
- the steel sheets for the automobile body also have been required to have excellent secondary work embrittlement resistance and fatigue properties of welded joints in terms of using conditions of the automobiles, and to have an appealing plated surface.
- steel sheets having enhanced formability and strength are produced in such a way of adding formability enhancing elements, that is, carbide and nitride formation elements such as Ti, Nb and the like, and strength enhancing elements, that is, solid solution strengthening elements such as Mn, P, Si and the like to a highly pure steel which is minimized in contents of impurities in the steel. Due to inherent restrictions in properties of the steel, however, it is difficult to enhance the formability and the strength at the same time.
- formability enhancing elements that is, carbide and nitride formation elements such as Ti, Nb and the like
- strength enhancing elements that is, solid solution strengthening elements such as Mn, P, Si and the like
- the steel sheet for extra deep drawing is produced using the highly pure steel, it commonly suffers from embrittlement of grain boundaries, which results in significant deterioration of secondary work embrittlement resistance and fatigue properties of welded joints.
- the steel sheets for deep drawing are produced using, so called, ultra-low carbon interstitial free (IF) steel, which is produced by adding the carbide and nitride formation elements such as Ti, Nb, and the like as a single component or a combination thereof to ultra-low carbon steel while lowering an amount of interstitial solid solution elements such as C or N to 50 ppm or less during a steel making process in order to ensure good formability.
- IF ultra-low carbon interstitial free
- the carbide and nitride formation elements such as Ti, Nb, and the like are added in an amount of 0.01 ⁇ 0.07% to the ultra-low carbon steel in order to ensure workability
- the steel lacks in the interstitial solid solution strengthening elements which serve to strengthen the grain boundaries, causing the secondary work embrittlement while deteriorating the fatigue properties at the spot welded joints.
- inventors of the present invention invented a high strength steel sheet for extra deep drawing useful for automobiles and the like, and a method for manufacturing the same disclosed in Korean Patent Laid-open Publication No. 2004-0002768 , which comprises, by weight%, C: 0.010% or less, Si: 0.02% or less, Mn: 1.5% or less, P: 0.03 - 0.15%, S: 0.02% or less, Sol.
- this method can enhance the workability by controlling Ti and Nb in combination, it fails to ensure the secondary work embrittlement and the fatigue properties which have been required for the steel plate of the automobile in recent years.
- the present invention has been made to solve the above problems, and it is an object of the present invention to provide a high strength steel sheet for deep drawing, which is controlled in contents of Ti, Al, B and N, and in contents of Nb, Al and C combinationally, while increasing the content of Al, which is advantageous in terms of formability and plating properties, and reducing the content of Ti, which is disadvantageous in terms of the plating properties, and the like, thereby providing excellent properties in terms of secondary work embrittlement resistance, and fatigue properties of welded joints as well as formability while exhibiting an appealing surface quality.
- a high strength steel sheet for deep drawing having excellent secondary work embrittlement resistance, fatigue properties and plating properties, comprising, by weight%: C: 0.010% or less, Si: 0.02% or less, Mn: 0.06 ⁇ 1.5%, P: 0.15% or less, S: 0.020% or less, Sol.
- Al 0.10 ⁇ 0.40%, N: 0.010% or less, Ti: 0.003 ⁇ 0.010%, Nb: 0.003 ⁇ 0.040%, B: 0.0002 ⁇ 0.0020%, optionally Mo ⁇ 0.05% and the balance of Fe and other unavoidable impurities, wherein the composition of Ti, Al, B, and N satisfies the relationship: 1.0 ⁇ (Ti[%]+Al[%]/16+6B[%])/3.43N[%] ⁇ 4.1, and wherein the composition of Nb, Al, and C satisfies the relationship: 0.7 ⁇ (Nb[%]+Al[%] /
- a method for manufacturing a high strength steel sheet for deep drawing having excellent secondary work embrittlement resistance, fatigue properties and plating properties comprises: reheating a steel slab at a temperature of 1,100 ⁇ 1,250 °C, the steel slab comprising, by weight%: C: 0.010% or less, Si: 0.02% or less, Mn: 0.06 ⁇ 1.5%, P: 0.15% or less, S: 0.020% or less, Sol.
- the steel sheets for deep drawing according to the present invention exhibit excellent secondary work embrittlement resistance, fatigue properties of welded joints, and an appealing plated surface as well as excellent formability compared with the conventional high strength steel sheets for deep drawing.
- a high strength steel sheet according to the present invention has characteristics in that it is controlled in contents of Ti, Al, B and N, and in contents of Nb, Al and C combinationally, while increasing the content of Al, which is advantageous in terms of formability and plating properties, and reducing the content of Ti, which is disadvantageous in terms of the plating properties, and the like, thereby exhibiting excellent properties in terms of secondary work embrittlement resistance, fatigue properties of welded joints and plating properties as well as formability.
- the steel sheet according to the present invention will be described in terms of composition and manufacturing method hereinafter.
- C acts as an interstitial solid solution element in steel, and obstructs formation of ⁇ 111 ⁇ texture, which is advantageous in terms of workability in the course of forming the texture in a steel sheet upon cold rolling and annealing.
- carbon content exceeds 0.010%, it is necessary to increase the contents of Ti and Nb which are carbide and nitride formation elements, causing a disadvantage in terms of manufacturing costs.
- the carbon content is preferably 0.010% or less.
- Si is an element which causes a defect of surface scale. If silicon content exceeds 0.02%, there arise problems such as temper color upon annealing, and non-plated parts upon plating. Thus, the silicon content is preferably 0.02% or less.
- Mn is a substitutional solid solution strengthening element for ensuring strength. If Mn content is less than 0.06%, the steel suffers from embrittlement due to S in the steel, whereas, if the Mn content exceeds 1.5%, an r-value of the steel is rapidly deteriorated along with elongation. Thus, the Mn content is preferably in the range of 0.06 ⁇ 1.5%.
- P is also a representative solid solution strengthening element which is added to the steel along with Mn for increasing the strength.
- P is added to Ti-Nb added steel as in the steel of the present invention, it results in growth of the ⁇ 111 ⁇ texture, advantageous in terms of the r-value, through grain refinement, grain boundary segregation, and the like.
- P content exceeds 0.15%, the steel suffers from rapid reduction in elongation along with significant increase in brittleness.
- the P content is preferably in the range of 0.15% or less.
- S content in the steel is generally restricted to a low degree of 0.005% or less. According to the present invention, however, since the steel contains Mn, all amounts of S in the steel are precipitated as MnS, thereby enabling deterioration of formability due to solid solution S to be avoided.
- S content is preferably 0.020% or less, which deviates from a region causing edge cracks during rolling.
- Sol. Al content of the steel is generally controlled to be in the range of 0.02 - 0.07% while dissolved oxygen in the steel is maintained in a sufficiently low state in consideration of manufacturing costs.
- Sol. Al serves to allow deep drawability to be stably secured at a lower annealing temperature.
- Sol. Al diffuses to the surface of the steel along the grain boundaries, and makes a plated layer dense, thereby enhancing powdering resistance of the steel.
- the Sol. Al content is 0.10% or more in the steel, it coarsens the precipitates in the steel, remarkably obstructs effect of suppressing recrystallization by P, thereby activating the recrystallization, and aids in development of the ⁇ 111 ⁇ texture and enhancement of the powdering resistance. If the Sol. Al content exceeds 0.40%, it causes an increase of the costs, and deterioration in efficiency of continuous casting operation.
- the Sol. Al content is preferably in the range of 0.10 ⁇ 0.40%.
- the Sol. Al content influences formation of Ti or Nb-based precipitates as the carbide and nitride such that the precipitates become coarsened, it serves as a critical component, which provides further enhanced formability of the steel with small added amounts of Ti and Nb in comparison to the conventional IF steel.
- N generally exists in a solid solution state, and deteriorates the formability of the steel. If N content exceeds 0.010%, it is necessary to increase added amounts of Ti and Nb for fixing N as precipitates. Thus, the N content is preferably 0.010% or less.
- Ti is a very important element in terms of the formability. In order to provide effect of enhancing the formability (in particular, r-value), Ti must be added to the steel in an amount of 0.003% or more. However, if Ti content exceeds 0.010%, it is disadvantageous in terms of manufacturing costs and plating properties in galvannealing. Thus, the Ti content is preferably in the range of 0.003 - 0.010%.
- Nb is also a very important element in terms of the formability like Ti.
- Nb In order to provide the effect of enhancing the formability (in particular, r-value), Nb must be added to the steel in an amount of 0.003% or more.
- Nb content exceeds 0.040%, it is disadvantageous in terms of the manufacturing costs and the plating properties.
- the Nb content is preferably in the range of 0.003 - 0.040%.
- B is a grain boundary strengthening element, and effective to enhance fatigue properties of spot welded joints while preventing grain boundary embrittlement by P. If B content is less than 0.0002%, the steel fails to achieve the effect described above, whereas, if the B content exceeds 0.0020%, there arise problems of rapid reduction in the formability, and deterioration in surface properties of plated steel sheet. Thus, the B content is preferably 0.0002 - 0.0020%.
- the steel sheet comprises the balance of Fe and other unavoidable impurities in addition to the above components.
- the steel sheet of the present invention may further comprise Mo in order to further enhance the secondary work embrittlement resistance and the plating properties.
- Mo content is preferably 0.05% or less. The reason is that, if the Mo content exceeds 0.05%, the effect of enhancing the secondary work embrittlement resistance and the plating properties by the Mo content is significantly reduced, and it is disadvantageous in terms of the manufacturing costs.
- the present invention in order to simultaneously secure the formability, plating properties, secondary work embrittlement resistance and fatigue properties of the steel which has the composition with a low Ti content and a high Al content as described above, it is necessary to control the contents of Al, B and N in combination to addition of Ti as in the following Expression 1.
- the present invention since the Ti content is low in comparison to the conventional steel sheet, there is a high possibility of deterioration of formability.
- the present invention suggests the following Expression 1:
- a calculated value of the expression is less than 1.0, the steel suffers from not only the aging phenomenon and the deterioration in drawability, but also failure in ensuring the secondary work embrittlement resistance and the fatigue properties.
- the calculated value exceeds 4.1, the steel suffers from deterioration in the plating properties and the stretching properties. Accordingly, it is preferably to control the content of Ti, Al, B and N so as to satisfy the relationship of 1.0 ⁇ (Ti[%]+Al[%]/16+6B[%])/3.43N[%] ⁇ 4.1
- the present invention in order to ensure the deep drawability and the stretching properties more stably, it is necessary to control the contents of the components so as to satisfy the following Expression 2. Specifically, due to the low Ti content of the steel according to the present invention, it is necessary to further ensure the deep drawability and the stretching properties. To this end, the present invention controls the contents of Nb, Al and C in combination according to the following Expression 2:
- Nb-Ti-Al-N-C based composite precipitates are formed.
- an average size of Nb-Ti-Al-N-C based composite precipitates is controlled to be 40 ⁇ or more, it is more preferable since it can further enhance the formability of the steel sheet.
- the formability and the plating properties can be further enhanced by restricting a fraction of Ti 4 C 2 S 2 to be 50% or more and a fraction of TiC to be below 5% among the Nb-Ti-Al-N-C based precipitates.
- Ti 4 C 2 S 2 is a precipitate advantageous in terms of the formability and the plating properties desired to be obtained by the present invention, if the fraction of Ti 4 C 2 S 2 is controlled to be 50% or more, it is possible to secure further enhanced formability and plating properties.
- TiC is a precipitates disadvantageous in terms of the plating properties, if the fraction of TiC is restricted to be below 5%, it is possible to secure further enhanced plating properties.
- the control of the composite precipitates as described above is closely related to a ratio of a reduction amount of rough rolling to a reduction amount of finish rolling (also hereinafter referred to as a reduction amount ratio) in hot rolling when manufacturing of the steel sheet according to the present invention, which will be described below.
- the steel sheet can be produced to have a desired tensile strength by controlling the components to satisfy the above composition and the following Expression 3:
- the present invention it is possible to control the contents of the components such that a calculated value of 27.6 + 4.81Mn[%] + 90.7P[%] + 132Nb[% ] + 30Mo[%]+180B[%] is in the range of 28 ⁇ 50.
- This expression is a regression expression of tensile strength according to the present invention, which expresses an influential degree of each component to the tensile strength as a coefficient based on experience.
- a steel slab having the composition as described above is reheated to a temperature of 1,100 ⁇ 1,250 °C. If the reheating temperature is less than 1,100 °C, it is difficult to perform hot rolling, whereas, if the reheating temperature exceeds 1,250 °C, surface defects can be created.
- a finish rolling temperature is preferably controlled to be 880 °C or more. The reason is that, if the finish rolling temperature is less than 880 °C, mixed grains are created, causing negative properties of products.
- a ratio of a reduction amount of rough rolling to a reduction amount of finish rolling that is, a reduction amount ratio is suitably controlled during the hot rolling.
- the reduction amount ratio is preferably controlled in the range of 1.0 - 3.5.
- the reason is that, if the reduction amount ratio is less than 1.0, the reduction amount of the finish rolling is significantly increased, causing an increase of load while making it difficult to control the fraction of Ti 4 C 2 S 2 among the precipitates to be 50% or more and to control the fraction of TiC to be below 5%.
- the reduction amount ratio exceeds 3.5, the effect of improving the r-value is negligible. Controlling of the reduction amount ratio will be described in detail hereinafter.
- Ti, Nb and the like react with impurity solid solution elements, and form precipitates, size and distribution of which significantly influence the formability of the final cold rolled products.
- the precipitates mainly having a size of several hundreds of or more are uniformly distributed instead of ultra fine precipitates having a size of several dozens of or less in a state wherein all the impurity elements such as C, N, S and the like in the hot rolled steel sheet are fixed as the precipitates, the r-value of the cold rolled steel sheet as the final product is remarkably improved.
- the size and distribution of the precipitates in the ultra-low carbon steel significantly depend on a hot rolling temperature and the reduction amount. Since formation of the precipitates is promoted via dynamic precipitation during the rolling process, an increase of the reduction amount in the temperature region of most actively enabling the precipitation results in easy formation of the precipitates.
- the increase in reduction amount of the finish rolling can cause an increase in fraction of Ti 4 C 2 S 2 which is advantageous in terms of the formability and the plating properties, and a decrease in fraction of TiC, which is disadvantageous in terms of the plating properties.
- the reduction amount ratio is restricted due to the following reasons: increasing the reduction amount of the finish rolling serves not only to allow the precipitates mainly having the size of several hundreds of or more to be distributed in the steel sheet without forming the solid solution elements therein, but also to increase the fraction of the precipitate, which is advantageous in terms of the formability and the plating properties, while decreasing the fraction of the precipitate, which is disadvantageous in terms of the plating properties, thereby improving the r-value and the plating properties of the final product.
- the coil hot-rolled steel sheet is subjected to cold rolling and continuous annealing.
- a reduction ratio of the cold rolling is preferably restricted to be 65% or more since the reduction ratio below 65% makes it difficult to obtain a high r-value of 1.9 or more.
- the continuous annealing is preferably performed at a temperature of 780 ⁇ 860 °C.
- an annealing temperature less than 780 °C makes it difficult to obtain a high r-value of 1.9 or more, and an annealing temperature above 860 °C provides a high possibility of causing problems to threading of strips during the operation due to high temperature annealing. Since the continuous annealing temperature of the present invention is significantly lower than a temperature region (880 - 930 °C) used by the conventional method for manufacturing the steel sheet for deep drawing, it is advantageous in manufacturing cost, and provides excellent producibility.
- the cold rolled steel sheet produced as above can be subjected to a typical plating process, if necessary.
- the plating process may be, for example, galvanizing, galvannealing, and the like.
- the fatigue properties were evaluated under a condition wherein, when applying a load repetitiously a total of ten million times to point welded samples with a cycle of 60 Hz, the samples did not fail.
- the powdering resistance was evaluated according to a detached ratio of a plated layer due to cupping, which was calculated in terms of a weight ratio. Table 1 Steel No. Components Exp. 1 Exp. 2 Exp.
- Inventive steels 1 ⁇ 16 satisfying the conditions of the present invention exhibit excellent properties in terms of secondary work embrittlement resistance, fatigue properties, and plating properties (powdering resistance) as well as formability.
- Comparative steels 1 ⁇ 12 not satisfying the conditions of the present invention in terms of composition and relations between the components exhibit deteriorated properties in terms of secondary work embrittlement resistance, fatigue properties, and plating properties (powdering resistance) as well as formability compared with the inventive steels.
- Comparative steels 1, 4, 7 and 10 satisfying the composition according to the present invention while not satisfying the relations between the components elongation, r-value, secondary work embrittlement resistance and fatigue properties are lower than the inventive steels.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
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- Heat Treatment Of Sheet Steel (AREA)
- Shaping Metal By Deep-Drawing, Or The Like (AREA)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
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KR1020050061691A KR100685030B1 (ko) | 2005-07-08 | 2005-07-08 | 내2차가공취성, 피로특성 및 도금특성이 우수한 심가공용박강판 및 그 제조방법 |
PCT/KR2006/002657 WO2007007983A1 (en) | 2005-07-08 | 2006-07-07 | Steel sheet for deep drawing having excellent secondary work embrittlement resistance, fatigue properties and plating properties, and method for manufacturing the same |
Publications (3)
Publication Number | Publication Date |
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EP1920078A1 EP1920078A1 (en) | 2008-05-14 |
EP1920078A4 EP1920078A4 (en) | 2010-03-24 |
EP1920078B1 true EP1920078B1 (en) | 2012-03-21 |
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Family Applications (1)
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EP06769200A Active EP1920078B1 (en) | 2005-07-08 | 2006-07-07 | Steel sheet for deep drawing having excellent secondary work embrittlement resistance, fatigue properties and plating properties, and method for manufacturing the same |
Country Status (7)
Country | Link |
---|---|
US (1) | US20080196799A1 (ja) |
EP (1) | EP1920078B1 (ja) |
JP (1) | JP4848423B2 (ja) |
KR (1) | KR100685030B1 (ja) |
CN (1) | CN101218363B (ja) |
AT (1) | ATE550448T1 (ja) |
WO (1) | WO2007007983A1 (ja) |
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KR20070038730A (ko) | 2005-10-06 | 2007-04-11 | 주식회사 포스코 | 항복비가 우수한 석출강화형 냉연강판 및 그 제조방법 |
JP5765080B2 (ja) * | 2010-06-25 | 2015-08-19 | Jfeスチール株式会社 | 伸びフランジ性に優れた高強度熱延鋼板およびその製造方法 |
CN102912226A (zh) * | 2012-10-17 | 2013-02-06 | 首钢总公司 | 一种抗二次加工脆性dc06汽车用钢及其生产方法 |
CN106191368B (zh) * | 2015-04-30 | 2018-06-26 | 上海梅山钢铁股份有限公司 | 一种高铝超低钛钢水的生产方法 |
KR102484978B1 (ko) * | 2020-12-11 | 2023-01-05 | 주식회사 포스코 | 내파우더링성이 우수한 고강도 합금화 용융아연도금강판 및 그 제조방법 |
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JP2752657B2 (ja) * | 1988-10-13 | 1998-05-18 | 川崎製鉄株式会社 | 深絞り成形性に優れた軟質熱延鋼板 |
JP2582894B2 (ja) * | 1989-04-04 | 1997-02-19 | 株式会社神戸製鋼所 | 深絞り用熱延鋼板及びその製法 |
JP3049104B2 (ja) * | 1991-03-13 | 2000-06-05 | 川崎製鉄株式会社 | 深絞り用高張力冷延鋼板の製造方法 |
JP2781297B2 (ja) * | 1991-10-29 | 1998-07-30 | 川崎製鉄株式会社 | 耐2次加工脆性に優れ面内異方性の少ない冷延薄鋼板の製造方法 |
JP3234644B2 (ja) | 1992-08-10 | 2001-12-04 | 川崎製鉄株式会社 | 耐二次加工脆性に優れる高r値高張力冷延鋼板及びその製造方法 |
US5690755A (en) * | 1992-08-31 | 1997-11-25 | Nippon Steel Corporation | Cold-rolled steel sheet and hot-dip galvanized cold-rolled steel sheet having excellent bake hardenability, non-aging properties at room temperature and good formability and process for producing the same |
CN1043905C (zh) * | 1993-10-05 | 1999-06-30 | 日本钢管株式会社 | 连续退火冷轧薄钢板及其制法 |
JPH07179946A (ja) | 1993-12-24 | 1995-07-18 | Kawasaki Steel Corp | 耐二次加工ぜい性に優れる高加工性高張力冷延鋼板の製造方法 |
JP3293015B2 (ja) * | 1995-02-23 | 2002-06-17 | 新日本製鐵株式会社 | 加工性の均一性に優れた冷延鋼板 |
JP3420370B2 (ja) * | 1995-03-16 | 2003-06-23 | Jfeスチール株式会社 | プレス成形性に優れた薄鋼板およびその製造方法 |
JP3295900B2 (ja) | 1996-07-02 | 2002-06-24 | 株式会社神戸製鋼所 | 耐二次加工脆性に優れた深絞り用高強度合金化溶融亜鉛めっき鋼板 |
JPH1060544A (ja) * | 1996-08-13 | 1998-03-03 | Kobe Steel Ltd | 高密度エネルギーの照射による薄鋼板の焼入れ強化方法 |
JPH1150211A (ja) * | 1997-08-05 | 1999-02-23 | Kawasaki Steel Corp | 深絞り加工性に優れる厚物冷延鋼板およびその製造方法 |
JP3840855B2 (ja) | 1999-02-15 | 2006-11-01 | Jfeスチール株式会社 | 耐二次加工脆性および成形性に優れた高強度薄鋼板およびその製造方法 |
JP3534023B2 (ja) | 1999-11-05 | 2004-06-07 | Jfeスチール株式会社 | 耐二次加工脆性に優れた高強度薄鋼板およびその製造方法 |
KR20010059365A (ko) * | 1999-12-30 | 2001-07-06 | 이구택 | 성형성이 우수한 고강도 냉연강판 및 그 제조방법 |
US20030015263A1 (en) * | 2000-05-26 | 2003-01-23 | Chikara Kami | Cold rolled steel sheet and galvanized steel sheet having strain aging hardening property and method for producing the same |
KR100470643B1 (ko) * | 2000-12-05 | 2005-03-07 | 주식회사 포스코 | 드로잉성 및 내2차 가공취성이 우수한 고강도 냉연강판 및그 제조방법 |
KR100530057B1 (ko) * | 2001-11-26 | 2005-11-22 | 주식회사 포스코 | 가공성 및 내2차가공취성이 우수한 고강도 냉연강판의제조방법 |
KR100544645B1 (ko) * | 2001-12-24 | 2006-01-24 | 주식회사 포스코 | 가공성이 우수한 복합조직 냉연강판 제조방법 |
EP1518001A4 (en) * | 2002-06-28 | 2006-01-11 | Posco | HIGH STRENGTH HIGH STRENGTH STEEL SHEET AND PROCESS FOR PRODUCING SAME |
KR100946067B1 (ko) * | 2002-12-27 | 2010-03-10 | 주식회사 포스코 | 내시효성이 우수한 용융도금용 소부경화형 냉연강판제조방법 |
US20070181232A1 (en) * | 2004-03-25 | 2007-08-09 | Posco | Cold rolled steel sheet and hot dipped steel sheet with superior strength and bake hardenability and method for manufacturing the steel sheets |
-
2005
- 2005-07-08 KR KR1020050061691A patent/KR100685030B1/ko active IP Right Grant
-
2006
- 2006-07-07 CN CN2006800250138A patent/CN101218363B/zh active Active
- 2006-07-07 EP EP06769200A patent/EP1920078B1/en active Active
- 2006-07-07 AT AT06769200T patent/ATE550448T1/de active
- 2006-07-07 JP JP2008520188A patent/JP4848423B2/ja active Active
- 2006-07-07 US US11/994,630 patent/US20080196799A1/en not_active Abandoned
- 2006-07-07 WO PCT/KR2006/002657 patent/WO2007007983A1/en active Application Filing
Also Published As
Publication number | Publication date |
---|---|
KR20070006393A (ko) | 2007-01-11 |
CN101218363B (zh) | 2010-12-08 |
WO2007007983A9 (en) | 2010-09-16 |
ATE550448T1 (de) | 2012-04-15 |
JP2009500524A (ja) | 2009-01-08 |
CN101218363A (zh) | 2008-07-09 |
US20080196799A1 (en) | 2008-08-21 |
KR100685030B1 (ko) | 2007-02-20 |
WO2007007983A1 (en) | 2007-01-18 |
EP1920078A4 (en) | 2010-03-24 |
EP1920078A1 (en) | 2008-05-14 |
JP4848423B2 (ja) | 2011-12-28 |
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