WO2006109522A1 - 溶融亜鉛めっき鋼板、および合金化溶融亜鉛めっき鋼板 - Google Patents
溶融亜鉛めっき鋼板、および合金化溶融亜鉛めっき鋼板 Download PDFInfo
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- WO2006109522A1 WO2006109522A1 PCT/JP2006/305955 JP2006305955W WO2006109522A1 WO 2006109522 A1 WO2006109522 A1 WO 2006109522A1 JP 2006305955 W JP2006305955 W JP 2006305955W WO 2006109522 A1 WO2006109522 A1 WO 2006109522A1
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- dip galvanized
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- galvanized steel
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/34—Methods of heating
- C21D1/42—Induction heating
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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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/52—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for wires; for strips ; for rods of unlimited length
- C21D9/54—Furnaces for treating strips or wire
- C21D9/56—Continuous furnaces for strip or wire
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Definitions
- the present invention relates to a hot dip galvanized steel sheet or an alloyed hot dip galvanized steel sheet.
- Steel sheets for structural members such as front side members, which play a role in absorbing energy at the time of a collision as an automobile skeleton member, are light weights for the purpose of improving fuel efficiency from the viewpoint of improving safety or as a countermeasure against environmental problems. From the viewpoint of achieving high strength, high strength is required.
- steel sheets for structural members are also required to have improved anti-rust properties.
- high-strength steel sheets are used as a base material, and high-temperature zinc galvanized surfaces are used. A strong steel plate is used.
- These high-strength galvanized high-strength steel sheets are the base material for which it is desirable that the galvanized galvanized layer be uniformly formed. It is required not to generate a part.
- the surface shape of the alloyed hot-dip galvanized steel sheet is made a shape that can easily hold a liquid lubricant such as a fouling oil. It has been proposed to reduce sliding resistance during press molding. However, in the method using a liquid lubricant, the lubricant is inferior due to uneven application of the lubricant or heat generated during continuous pressing. As a result, the slidability is easily lowered and the workability is likely to deteriorate.
- Patent Document 2 discloses controlling the degree of concentration of alloy elements in the very surface layer portion of the base material immediately below the plating layer. .
- the concentration degree of the alloy element is controlled, the plating adhesion may not be sufficiently improved, leaving room for improvement.
- Patent Document 3 As a technology that has excellent surface properties with no plating and non-alloying unevenness and that can also improve anti-plating resistance and slidability, the steel plate crystals are refined. As a result, a method for uniformly generating outburst and improving the plating peeling resistance has been disclosed. With this technology, many alloying elements must be added to refine the crystal of the steel sheet. As a result, the Fe concentration in the plating layer cannot be controlled properly, and sliding However, the powdering resistance sometimes deteriorated.
- Patent Document 1 Japanese Patent Laid-Open No. 2001-247949
- Patent Document 2 JP 2002-115039 A
- Patent Document 3 Japanese Patent Laid-Open No. 11 323492
- the present invention has been made in view of such a situation, and an object of the present invention is to provide a hot dip galvanized steel sheet using a steel sheet in which a non-plated portion is unlikely to occur when hot dip galvanizing is performed. There is to be.
- Another object of the present invention is to provide an alloyed hot dip galvanized steel sheet that is excellent in slidability and powdering resistance when hot galvanized and then alloyed. is there.
- Still another object is to provide a member for an automobile using the above-mentioned hot-dip galvanized steel sheet or an alloyed hot-dip galvanized steel sheet that has been further alloyed.
- the inventors of the present invention have repeatedly studied to provide a steel sheet that hardly generates a non-plated portion when hot-dip galvanized. As a result, it was found that if the component composition of the steel sheet is strictly defined and the balance of Cr and Mo is appropriately controlled, no unplated part will occur during hot dip galvanizing. [0012] In addition, the present inventors have also studied measures for improving the slidability and powdering resistance of an alloyed hot-dip galvanized steel sheet obtained by alloying a hot-dip galvanized steel sheet.
- the steel sheet used in the hot dip galvanized steel sheet according to the present invention is mass%, C: 0.06 to 0.15%, Mn: l to 3%, P: 0.01 to 0.05%, Cr : 0.03-1%, Mo: 0.03-1%, and A1: 0.02-0.15%, Si: 0.2% or less (including 0%), and S: 0.03% or less (including 0%)
- the gist is that the K value calculated from the following formula (1) is -2.0 or more.
- K value 3 X [Mo] _ 5 X [Cr core... (1)
- [element] indicates the content (% by mass) of each element.
- the steel sheet further contains, as other elements, mass%, Ti: 0.15% or less (excluding 0%), Nb: 0.15% or less (excluding 0%), and V: 0.15% or less ( It is preferable to contain at least one selected from the group consisting of (excluding 0%).
- the steel sheet further contains, as another element, in mass%, B: 0.01% (less than 0%), Ca,
- the steel sheet is the mass%, C: 0.06 to 0.15%, Mn: l to 3%, P: 0.01 to 0.05%, Cr: 0.03-1%, Mo: 0.03-1%, and ⁇ 1: 0 ⁇ 02-0.15%, Si: 0.2% or less (including 0%), and S: 0.03% or less (0% K value calculated from the following formula (1) is 1 or more 2.0,
- K value 3 X [Mo] _ 5 X [Cr core... (1)
- the main point is that the F value calculated from the following formula (2) satisfies 0.7 to 3.0.
- [element] represents the content (% by mass) of each element.
- the hot dip galvanized steel sheet and the alloyed hot dip galvanized steel sheet of the present invention can be preferably used as materials for automobile members.
- a steel sheet for hot dip galvanizing in which a non-plated portion is less likely to occur when hot galvanized by appropriately controlling the content balance of Mo and Cr among the constituent elements of the steel plate. Can provide.
- hot-dip galvanizing the hot-dip galvanized steel sheet it is possible to provide a hot-dip galvanized steel sheet with no unplated portions, and alloying the hot-dip galvanized steel sheet. By doing so, it is possible to provide an alloyed hot-dip galvanized steel sheet having excellent slidability and powdering resistance.
- Such a hot-dip galvanized steel sheet or an alloyed hot-dip galvanized steel sheet can be preferably used as a material for automobile members.
- FIG. 1 is an electron micrograph (drawing substitute photograph) of No. 3 in Table 2.
- FIG. 2 is a graph showing the relationship between the K value and Fe concentration and the presence or absence of non-plating.
- Fig. 3 is a graph showing the relationship between the F value and Fe concentration and the slidability or pudding resistance.
- the K value is less than -2.0, pinhole-shaped non-plated parts (unplated parts) frequently occur on the surface of the steel sheet when hot-dip galvanizing occurs, and the appearance quality is significantly impaired.
- the K value is preferably controlled to be _1.5 or more, more preferably 11 or more.
- [element] indicates the content (% by mass) of each element.
- Cr and Mo are elements that, when added in combination, form a composite oxide on the surface of the steel sheet and prevent the occurrence of non-plating. That is, for example, in a steel sheet containing Cr alone, non-plating is difficult to occur if the Cr content is up to 0.4%, but non-plating occurs when the Cr content is 0.4% or more. appear. However, if the forces Cr and Mo are added in combination, a composite oxide is formed on the surface of the steel sheet, preventing the occurrence of non-plating. Moreover, as will be apparent from the examples described later, when Cr and Mo are added in combination, the strength-elongation balance is improved and a steel sheet having both mechanical properties and plating properties is obtained.
- Mo are elements that improve the hardenability and have the effect of concentrating C in austenite to increase the stability of austenite.
- Cr is preferably 0.05% or more, more preferably 0.1% or more.
- Mo is preferably 0.05% or more, more preferably 0.1% or more.
- adding Cr or Mo in excess of 1% saturates the effect and increases costs, so the upper limit is 1%.
- the Cr content is preferably 0.9% or less, more preferably 0.8% or less.
- the Mo content is preferably 0.9% or less, more preferably 0.8% or less.
- the steel plate of the present invention contains, as other components, C: 0.06 to 0.15%, Mn: l to 3%, P: 0.01 to 0.05%, and ⁇ 1: 0 ⁇ 02- Contains 0.1%.
- C 0.06 to 0.15%
- Mn l to 3%
- P 0.01 to 0.05%
- ⁇ 1 0 ⁇ 02- Contains 0.1%.
- C is an important element for increasing the strength of the steel sheet, and also affects the amount of low-temperature transformation products (for example, bainite and martensite) and their form, and workability (elongation and stretch flangeability). To improve. If the C content is less than 0.06%, it will not be possible to secure a strength of 590 MPa or more. Therefore, the C content should be 0.06% or more.
- the C content is preferably 0.07% or more, more preferably 0.08% or more. If the C content exceeds 0.15%, the weldability is lowered when a high strength steel sheet with galvanized steel or high strength steel sheet with galvannealed alloy is used. C content is less than 0.14% More preferably, it is 0.13% or less.
- Mn is an important element for stabilizing austenite and ensuring the strength of the steel sheet itself.
- Mn is an element that improves hardenability, and acts usefully to obtain a desired metal structure. In order to exert such an effect, it is necessary to contain at least 1% of Mn.
- Mn content is 1.5. More preferably, it is at least 0, more preferably at least 1.8%. Higher Mn content is preferable, but if it exceeds 3%, not only the melting becomes difficult, but also the weldability of hot-dip galvanized high-strength steel sheets and galvannealed high-strength steel sheets is adversely affected. The effect is 3% or less.
- the Mn content is preferably 2.9% or less, more preferably 2.8% or less.
- P is an element that is fixed as a precipitate in the steel sheet and is effective in securing a balance of strength and elongation. In order to exert such an effect, it is necessary to contain 0.01% or more of P, and a preferable content is 0.015% or more. However, if the P content exceeds 0.05%, defects will occur, so the upper limit is 0.05%.
- the preferred content is 0.04% or less, more preferably 0.03% or less.
- A1 is an element to be contained for deoxidation, and is contained at least 0.02%.
- the preferred content is 0.03% or more, more preferably 0.04% or more. However, if the amount is too large, the surface properties and toughness are deteriorated by increasing the amount of oxide inclusions, so the upper limit is made 0.15%.
- a preferred content is 0.13% or less, and a more preferred content is 0.1% or less.
- Si and S are elements which are mixed as inevitable impurities, which are preferably basically not contained.
- Si should be suppressed to 0.2% or less and S should be suppressed to 0.03% or less.
- Si 0.2% or less (including 0%)
- Si is a harmful element that forms an oxide film (for example, Si02) on the surface of the steel sheet and degrades the wettability of the plating. Therefore, it is preferable not to contain Si as much as possible. 0 Keep it below 2%. It is preferable to keep it to 0.1% or less.
- S is the force that is fixed as MnS-based precipitates in the steel sheet.
- the amount increases, elongation and stretch flangeability deteriorate. Therefore, even if it is mixed as an inevitable impurity, it should be suppressed to 0.03% or less. Preferably, it should be suppressed to 0.015% or less.
- the high-strength steel sheet of the present invention satisfies the content range of the above-mentioned component elements, but as other elements, (a) Ti: 0.15% or less (not including 0%), Nb: 0.15 % (Less than 0%) and V: 0.15. / 0 or less ( 0, not including / o), at least one selected from the group consisting of: (b) B: 0.01% (not including 0%), (c) Ca: 0.01% or less (0% Etc.), etc. are preferable.
- the reason for specifying such a range is as follows.
- Ti, Nb, and V have precipitation strengthening and microstructure refinement effects, and are useful elements for increasing strength. In order to exert such an effect effectively, it is recommended to contain 0.01% or more (particularly preferably 0.02% or more) of each. However, if added in excess, the strength of the hot-rolled steel sheet will increase excessively, leading to shape defects during cold rolling, so each is made 0.15% or less (more preferably 0.13% or less).
- ⁇ is an element that enhances hardenability and improves the strength (TS and YS) of steel sheets.
- TS strength
- YS strength
- B be contained in an amount of 0.0005% or more in order to exert these effects effectively. More preferably, it is 0.001% or more.
- the content exceeds 0.01%, the toughness of the base metal deteriorates, so the B content is preferably suppressed to 0.01% or less. More preferably, it is 0.05% or less.
- Ca is an element that contributes to improving workability by spheroidizing the form of sulfide in steel. In order to effectively exert such effects, it is recommended to add 0.0003% or more (more preferably 0.0005% or more). However, the above effect is saturated even if added over 0.01%. So it is economically wasteful. A more preferable content is 0.05% or less.
- the remaining components of the high-strength steel sheet of the present invention are Fe and inevitable impurities, but do not inhibit the effects of the present invention, and may contain other elements within the range. .
- the galvannealed high-strength steel sheet obtained by alloying the hot-dip galvanized high-strength steel sheet cannot be said to have sufficiently improved slidability and powdering resistance. Tsutsu. Accordingly, the present inventors have focused on the composition of the alloyed hot-dip zinc plating layer after the alloying treatment and conducted various studies. As a result, a soft ⁇ phase (Fe Zn) is formed on the surface of the alloyed hot-dip zinc plating layer. It has been found that the slidability during pressing is significantly reduced when) is formed. on the other hand,
- the powdering resistance was found to be significantly reduced. It has also been clarified that the composition of the alloyed hot-dip zinc plating layer is affected by the alloying rate of the hot-dip zinc plating layer when alloying the high-strength steel plate with hot-dip zinc.
- the alloying rate was determined by the content of Mn, P, Cr, Mo, among the components of the high-strength steel sheet. Was found to be affected.
- Mn, P, Cr, and Mo are elements necessary for improving the hardenability of the steel sheet and ensuring the strength, but a slight change in content greatly affects the alloying rate of the molten zinc adhesive layer. It has an influence.
- the F value expressed by the following formula (2) was in the range of 0.7 to 3.0.
- the high-strength steel plate for galvanized zinc alloy is a high-strength steel plate for alloyed hot-dip galvanized steel that has been alloyed with the high-strength steel plate for hot-dip galvanized steel. I found out that it would be something.
- the detailed mechanism of how the elements contained in the high-strength steel sheet affect the alloying rate of the hot-dip zinc plating layer is not clear, but if the F value is less than 0.7,
- the soft ⁇ phase (FeZn), which is difficult to be alloyed with the molten zinc adhesive layer, is alloyed with molten zinc. It is formed on the surface of the adhesion layer. It is preferable to control the component composition so that the F value is 0.9 or more, more preferably 1.1 or more.
- the Fe concentration in the plating layer is preferably 7 to 15 mass%. If the Fe concentration is less than 7% by mass, the diffusion of Fe due to the alloying treatment is insufficient, so that the soft ⁇ phase (FeZn) is combined.
- the Fe concentration is 8% by mass or more, and more preferably 9% by mass or more.
- the Fe concentration exceeds 15% by mass, excessive Fe diffusion occurs, and a hard and brittle ⁇ phase (Fe Zn) is generated at the interface between the alloyed molten zinc plating layer and the base metal, which tends to cause powdering. Become. More preferred
- the new Fe concentration is 14% by mass or less, more preferably 13% by mass or less.
- the A1 content in the hot dip galvanizing bath may be adjusted. This point will be described later.
- the metallic structure of the base steel sheet in the hot dip galvanized steel sheet or alloyed hot dip galvanized steel sheet is preferably a mixed structure mainly composed of ferrite and martensite.
- a mixed structure mainly composed of ferrite and martensite By using a mixed structure mainly composed of ferrite and martensite, the overall strength of the plated steel sheet can be increased.
- the main body means that the ratio of the mixed structure to the entire metal structure of the base steel sheet is 70% or more in terms of area ratio. A more preferable area ratio is 80% or more.
- a metal structure such as pearlite or bainite may be generated.
- the ratio of ferrite to martensite is preferably about 90:10 to 25:75 in terms of area ratio.
- the metal structure of the base steel sheet may be observed at a magnification of 3000 times using a scanning electron microscope.
- the hot-dip galvanized high-strength steel plate or the alloyed hot-dip galvanized high-strength steel plate Tensile strength (TS) is about 590 ⁇ : 1180MPa, and the balance between strength and elongation is good (TS X E1 force 2000 or more), so it collides as a skeleton member of an automobile (for example, front side member) It can be preferably used as a material for automobile members such as members that play a role of absorbing energy.
- the method for producing the high-strength steel plate for hot dip galvanizing according to the present invention is not particularly limited. For example, after hot-rolling a steel slab (slab) satisfying the above component composition, it is heated at 700 ° C or lower. After rolling and pickling as necessary, it may be cold-rolled.
- Hot rolling may be performed according to a conventional method.
- the heating temperature of the steel slab is set to 1000 to: 1300 ° C, and also prevents the formation of a texture that impairs workability.
- the finishing temperature of hot rolling is set to 800 to 950 ° C, and the cooling rate after finishing rolling is preferably set to 30 to 120 ° C / sec in order to suppress the formation of pearlite.
- the scraping temperature is preferably 700 ° C or lower. This is because if the cutting temperature exceeds 700 ° C, the scale of the steel sheet surface becomes too thick and the pickling performance deteriorates.
- the lower limit of the milling temperature is not particularly limited. However, if the temperature is too low, the steel sheet becomes too hard and cold rolling properties deteriorate, so the lower limit is about 250 ° C.
- a preferred scraping temperature is 400 ° C or higher.
- pickling is performed according to a conventional method, followed by cold rolling.
- the cold rolling rate should be 30% or more. In order to reduce the cold rolling rate to less than 30%, it is necessary to reduce the thickness of the hot-rolled steel sheet, and it takes too much time force S for pickling, resulting in lower productivity.
- the method for producing the high-strength steel sheet with galvanized zinc or high-strength steel sheet with galvannealed alloy according to the present invention is not particularly limited, and the high-strength steel sheet with galvanized zinc is, for example, cold rolled by the above procedure. Then, after soaking at a temperature above the Acl point in a continuous hot dip galvanizing line, it is cooled to the plating bath temperature at an average cooling rate of i ° c / sec or higher, and hot galvanized galvanizing is applied to the surface of the high-strength steel sheet. Obtained by coating.
- high-strength steel plate with alloyed hot-dip galvanized steel is obtained by subjecting the high-strength steel plate with hot-dip galvanized steel obtained in the above procedure to alloying according to a conventional method, and then an average cooling rate of 5 ° C / sec or more. Cool it in
- the soaking temperature in the above-mentioned continuous hot dip galvanizing line may be a point A or higher.
- the upper limit of the soaking temperature is not particularly limited, but is generally 900 ° C or lower.
- the holding time during soaking is not particularly limited, and may be, for example, about 10 sec or more.
- the plate After soaking, the plate is cooled to a plating bath temperature (400 to 500 ° C, preferably 440 to 470 ° C) at a cooling rate of 1 ° C / sec or more, and then plated.
- a plating bath temperature 400 to 500 ° C, preferably 440 to 470 ° C
- the cooling rate is preferably 5 ° C / sec or more. Although the upper limit of the cooling rate is not specified, it is 50 considering the ease of controlling the plate temperature and the equipment cost. C / sec is good.
- the composition of the plating bath is not particularly limited, and a known hot dip galvanizing bath may be used.
- the A1 content in the plating bath is preferably 0.05-0.2%.
- A1 is an element that acts to control the alloying rate of the hot dip galvanized layer.
- the surface of the steel plate ie, the steel plate and the hot dip galvanized layer.
- An Fe-A1 metal layer is formed on the
- A1 is less than 0.05%, the Fe—A1 alloy layer is too thin, so when the steel sheet is immersed in a tanning bath, alloying of the steel sheet and zinc proceeds immediately.
- the more preferable A1 content is 0.07% or more.
- the Fe-A1 alloy layer becomes too thick, which prevents the alloying of Fe and Zn in the alloying process and delays the alloying of the molten zinc plating layer. To do. Therefore, in order to proceed with alloying, it is necessary to lengthen the alloying line or separately perform alloying treatment at high temperature.
- a more preferable A1 content is 0.18% or less.
- heating is performed to about 500 to 750 ° C (preferably about 500 ° C to 600 ° C) according to a conventional method.
- the heating hand when performing alloying treatment The stage is not particularly limited, and various conventional methods (for example, gas heating or induction heater heating) can be used.
- a mixed structure mainly composed of ferrite and martensite can be obtained by cooling to room temperature at a cooling rate of 5 ° C / sec or more.
- a slab obtained by melting a steel having the composition shown in Table 1 (the balance being Fe and inevitable impurities) and forging the molten steel was heated to 1150 ° C, and finished at a finishing temperature of 870 to 900 ° C. .
- the steel sheet was cold rolled to a thickness of 1.4 mm at a cold rolling rate of 46% to produce a cold rolled steel sheet.
- the obtained cold-rolled steel sheet was heated to 830 ° C in a continuous hot-dip galvanizing line, held at this temperature for 40 seconds, soaked, and cooled at an average cooling rate of 25 ° C / sec. Immerse in the plating bath.
- a known hot dip galvanizing bath was used as the plating bath. However, the A1 content was 0.13%.
- the plating bath temperature was set to 450 to 470 ° C., and this was immersed in this plating bath for 3 seconds for hot dip zinc plating.
- alloying treatment was performed, cooling to room temperature at a cooling rate of 30 ° C / sec or more, and then tempering at a reduction rate of 1.0% Rolled to obtain a galvannealed steel sheet.
- the metallographic structure in the center part of the thickness of the base steel sheet was observed using a scanning electron microscope (SEM).
- SEM scanning electron microscope
- the observation magnification was 3000 times.
- Fig. 1 shows an electron micrograph of No. 3 in Table 2 below as a drawing substitute photo.
- the alloyed hot-dip galvanized layer was dissolved in hydrochloric acid, and then the Fe concentration was measured by atomic absorption analysis. The results are shown in Table 2 below.
- TS X E1 was calculated, and the strength-elongation balance was evaluated. The results are shown in Table 2 below. TS X E1 force S12000 or higher was accepted and less than 12000 was rejected.
- the plating property was evaluated by visually observing the presence or absence of non-plated portions.
- Table 2 shows the evaluation results when the unplated part is not recognized as acceptable ( ⁇ ) and when the unplated part is recognized as unacceptable (X).
- Sliding performance is about 1 coating of anti-fouling oil (manufactured by Pachin Ischi Kosan Co., Ltd., “Knox Last 550HN (trade name)”) on the front and back of alloyed hot-dip galvanized steel sheet (test piece).
- ⁇ After coating at 5 g / m 2 , a surface pressure of about 30 N / mm 2 was pressed from both sides of the specimen using a 20 mm square tool.
- Friction coefficient F / 2P) was calculated based on the load (P) and the pull-out load (F) of the specimen, and this was used as an index for evaluation of slidability. As the evaluation criteria, the case where the coefficient of friction / was 0.20 or less was accepted, and the case where ⁇ was more than 0.20 was rejected. The results are shown in Table 2 below.
- FIG. 2 is a graph showing the relationship between the K value and Fe concentration and the occurrence of non-plating.
- ⁇ and ⁇ ⁇ show examples with no plating
- ⁇ and X show examples with no plating.
- ⁇ is an example in which powdering resistance is unacceptable
- ⁇ is an example in which slidability is unacceptable.
- ⁇ is an example in which slidability is also rejected.
- FIG. 3 is a graph showing the relationship between the F value and Fe concentration and the slidability or powdering resistance.
- ⁇ indicates that the slidability and powdering resistance are good
- X indicates that the slidability or powdering resistance is poor.
- ⁇ is an example in which slidability and anti-powdering properties are good but non-plating occurs.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Coating With Molten Metal (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
Claims
Priority Applications (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP20060729903 EP1865084A4 (en) | 2005-03-31 | 2006-03-24 | HOT DIP GALVANIZED STEEL SHEET AND HOT DIP GALVANIZED STEEL SHEET |
US11/908,431 US20090025831A1 (en) | 2005-03-31 | 2006-03-24 | Hot-dip galvanized steel sheet and galvannealed steel sheet |
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JP2005104799A JP3889767B2 (ja) | 2005-03-31 | 2005-03-31 | 溶融亜鉛めっき用高強度鋼板 |
JP2005-104799 | 2005-03-31 |
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WO2006109522A1 true WO2006109522A1 (ja) | 2006-10-19 |
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PCT/JP2006/305955 WO2006109522A1 (ja) | 2005-03-31 | 2006-03-24 | 溶融亜鉛めっき鋼板、および合金化溶融亜鉛めっき鋼板 |
Country Status (6)
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US (1) | US20090025831A1 (ja) |
EP (1) | EP1865084A4 (ja) |
JP (1) | JP3889767B2 (ja) |
KR (1) | KR100917504B1 (ja) |
CN (1) | CN100523258C (ja) |
WO (1) | WO2006109522A1 (ja) |
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JP4788291B2 (ja) * | 2005-10-27 | 2011-10-05 | Jfeスチール株式会社 | 伸びフランジ成形性に優れた高強度溶融亜鉛めっき鋼板の製造方法 |
JP5257981B2 (ja) * | 2007-07-11 | 2013-08-07 | Jfeスチール株式会社 | プレス成形性に優れた高強度溶融亜鉛めっき鋼板の製造方法 |
JP5272412B2 (ja) * | 2008-01-17 | 2013-08-28 | Jfeスチール株式会社 | 高強度鋼板およびその製造方法 |
EP2123786A1 (fr) * | 2008-05-21 | 2009-11-25 | ArcelorMittal France | Procédé de fabrication de tôles d'aciers dual phase laminées à froid à trés haute résistance et tôles ainsi produites |
KR20100034118A (ko) | 2008-09-23 | 2010-04-01 | 포항공과대학교 산학협력단 | 마르텐사이트 조직을 가진 초고강도 용융아연도금 강판 및 그 제조 방법 |
JP5394709B2 (ja) * | 2008-11-28 | 2014-01-22 | 株式会社神戸製鋼所 | 耐水素脆化特性および加工性に優れた超高強度鋼板 |
WO2012144028A1 (ja) | 2011-04-20 | 2012-10-26 | 株式会社神戸製鋼所 | めっき密着性に優れた合金化溶融亜鉛めっき高張力鋼板、およびその製造方法 |
JP6228741B2 (ja) * | 2012-03-27 | 2017-11-08 | 株式会社神戸製鋼所 | 板幅方向における中央部と端部の強度差が少なく、曲げ加工性に優れた高強度溶融亜鉛めっき鋼板、高強度合金化溶融亜鉛めっき鋼板、およびこれらの製造方法 |
JP6246621B2 (ja) * | 2013-05-08 | 2017-12-13 | 株式会社神戸製鋼所 | 引張強度が1180MPa以上の強度−曲げ性バランスに優れた溶融亜鉛めっき鋼板もしくは合金化溶融亜鉛めっき鋼板 |
KR102193424B1 (ko) * | 2016-07-15 | 2020-12-23 | 닛폰세이테츠 가부시키가이샤 | 용융 아연 도금 강판 |
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- 2006-03-24 EP EP20060729903 patent/EP1865084A4/en not_active Withdrawn
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Also Published As
Publication number | Publication date |
---|---|
EP1865084A1 (en) | 2007-12-12 |
US20090025831A1 (en) | 2009-01-29 |
EP1865084A4 (en) | 2010-07-28 |
KR100917504B1 (ko) | 2009-09-16 |
CN101115857A (zh) | 2008-01-30 |
CN100523258C (zh) | 2009-08-05 |
JP3889767B2 (ja) | 2007-03-07 |
KR20070107174A (ko) | 2007-11-06 |
JP2006283128A (ja) | 2006-10-19 |
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