WO2016104879A1 - 프레스성형시 내파우더링성이 우수한 hpf 성형부재 및 이의 제조방법 - Google Patents
프레스성형시 내파우더링성이 우수한 hpf 성형부재 및 이의 제조방법 Download PDFInfo
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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
- C22C38/18—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
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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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/012—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of aluminium or an aluminium alloy
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- 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
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—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
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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
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- 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
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- C—CHEMISTRY; METALLURGY
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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
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- 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
- C23C2/12—Aluminium or alloys based thereon
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- 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
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- C23C2/285—Thermal after-treatment, e.g. treatment in oil bath for remelting the coating
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- 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
- C23C2/26—After-treatment
- C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
- C23C2/29—Cooling or quenching
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- 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
- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
- C23C2/40—Plates; Strips
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Definitions
- the present invention relates to the production of an HPF molded member having an aluminum plating layer on its surface, and more particularly, to an HPF molded member having excellent powdering resistance during press molding by minimizing breakage and powdering of the plating layer during press molding. It relates to a manufacturing method.
- Steel plate for aluminum plating HPF (HOT PRESS FORMING) is manufactured by immersing plated steel with high quenchability in an Al-based plating bath, and plated steel sheet having Al plating layer on its surface is subsequently hot pressed. It is widely used in the manufacture of automobile members having a complex shape and strength of 1300 MPa or more.
- the plating layer includes an alloying layer containing an intermetallic compound composed of FeAl, Fe2Al5, etc. as an upper layer, and a diffusion layer consisting of 80 to 95 wt% Fe (hereinafter, all steel components are wt%) as a lower layer.
- an alloying layer containing an intermetallic compound composed of FeAl, Fe2Al5, etc. as an upper layer
- a diffusion layer consisting of 80 to 95 wt% Fe hereinafter, all steel components are wt%)
- all steel components are wt%
- the upper alloying layer of the plating layer has brittleness as compared to the diffusion layer, there is a disadvantage in that it is difficult to continuously press molding because it is dropped from the plating layer during the press molding and adsorbed on the press surface.
- the present invention is to overcome the above limitations, in particular, by optimizing the thickness of the alloying layer, the fraction of the tau in the plating layer and the content of Si, Cr, it is possible to minimize the adsorbed on the mold surface due to the plating layer is eliminated during press molding
- the purpose is to provide an HPF molded member.
- Another object of the present invention is to provide a method of manufacturing the HPF molded member.
- the base steel sheet has a weight% of C: 0.18 to 0.25%, Si: 0.1 to 1.0%, Mn: 0.9 to 1.5%, P: 0.03% or less, S: 0.01% or less, Al: 0.01 ⁇ 0.05%, Cr: 0.05 ⁇ 0.5%, Ti: 0.01 ⁇ 0.05%, B: 0.001 ⁇ 0.005, N: 0.009% or less, balance Fe and other impurities It includes;
- the hot dip plating layer is composed of a soft diffusion layer and a hard alloy layer;
- the tau phase is present in the alloy layer in the range of 10% to 30% by area%;
- the alloy layer is composed of the tau phase by its own weight percent, including 10% or more of Si and 0.2% or more of Cr so that the thickness thereof is 35 ⁇ m or less. It is about.
- the base steel sheet may be a cold rolled steel sheet or a hot rolled steel sheet.
- the tau phase is preferably composed of Si: 10-12%, Mn + Cr: 1.3-2.0%, residual Fe and Al in its own weight%.
- the thickness ratio of the alloy layer / diffusion layer in the hot dip plating layer satisfies 1.5 to 3.0.
- the tau phase is formed in the boundary between the alloy layer and the diffusion layer and inside the alloy layer, and the tau phase formed in the alloy layer preferably has a band shape connected to each other in a section of 50% or more in a direction perpendicular to the thickness of the plating layer.
- the steel sheet is preferably Mo + W: 0.001 ⁇ 0.5% additionally included.
- the base steel sheet is Nb, Zr 'or one or more of the sum of V: 0.001 ⁇ 0.4% is preferably further included in the range.
- the base steel sheet is Cu + Ni: It is preferably further included in the range 0.005 ⁇ 2.0%.
- the base steel sheet preferably further comprises at least 0.03% of one or more of Sb, Sn or Bi.
- the composition of the components by weight including Si 9-11%, Fe: less than 3%, balance Al and other unavoidable impurities Immersing in a molten aluminum plating bath formed by the molten aluminum plating process;
- Alloying the molten aluminum plated layer on the surface by heating the molten aluminum plated steel sheet to a temperature of 880 to 930 ° C., and then maintaining the molten aluminum plated steel sheet for a predetermined time; And
- the present invention relates to a method for manufacturing an HPF molded member having excellent powdering resistance during press molding, including a step of hot forming the alloyed molten aluminum plated steel sheet and simultaneously quenching it to a temperature range of 300 ° C. or less. .
- the cooling is preferably performed at an average cooling rate of 15 ° C./s or more until the plating layer is solidified after the hot dip plating.
- the alloyed molten aluminum plating layer is composed of a soft diffusion layer and a hard alloy layer;
- the tau phase is present in the alloy layer in the range of 10% to 30% by area%;
- the said tau phase is comprised by itself weight%, 10% or more of Si, and 0.2% or more of Cr so that the said alloy layer may be 35 micrometers or less in thickness.
- the steel sheet may be a cold rolled steel sheet or a hot rolled steel sheet.
- the tau phase is preferably composed of Si: 10-12%, Mn + Cr: 1.3-2.0%, residual Fe and Al in its own weight%.
- the thickness ratio of the alloy layer / diffusion layer in the molten aluminum plating layer satisfies 1.5 to 3.0.
- the tau phase is formed in the boundary between the alloy layer and the diffusion layer and inside the alloy layer, and the tau phase formed in the alloy layer preferably has a band shape connected to each other in a section of 50% or more in a direction perpendicular to the thickness of the plating layer.
- the step of cooling to a temperature range of 700 ⁇ 780 °C may further include.
- the cooling rate in the range of 20 ⁇ 100 °C / s.
- Alloying the molten aluminum plated layer on the surface by heating the molten aluminum plated steel sheet to a temperature of 880 to 930 ° C., and then maintaining the molten aluminum plated steel sheet for a predetermined time; And
- the present invention relates to a method for manufacturing an HPF molded member having excellent powdering resistance during press molding, including a step of hot forming the alloyed molten aluminum plated steel sheet and simultaneously quenching it to a temperature range of 300 ° C. or less. .
- the alloyed molten aluminum plating layer is composed of a soft diffusion layer and a hard alloy layer;
- the tau phase is present in the alloy layer in the range of 10% to 30% by area%;
- the said tau phase is comprised by itself weight%, 10% or more of Si, and 0.2% or more of Cr so that the said alloy layer may be 35 micrometers or less in thickness.
- the steel sheet may be a cold rolled steel sheet or a hot rolled steel sheet.
- the tau phase is preferably composed of Si: 10-12%, Mn + Cr: 1.3-2.0%, residual Fe and Al in its own weight%.
- the thickness ratio of the alloy layer / diffusion layer in the molten aluminum plating layer satisfies 1.5 to 3.0.
- the present invention having the above-described configuration, by optimizing the thickness of the alloying layer constituting the molten aluminum plating layer, the fraction of the tau phase in the plating layer and the composition of the tau phase, etc., it is possible to minimize that the plating layer is dropped and adsorbed on the mold surface during press molding. It is possible to effectively provide an HPF molded member.
- FIG. 1 is a tissue photograph showing a cross section of the plating layer after hot pressing in an embodiment of the present invention.
- FIG. 2 is a structure photograph showing a cross section of the plating layer after hot pressing in a comparative example.
- the present inventors have repeatedly conducted research and experiments to solve these problems, and as a result, have sought ways to reduce the thickness of the alloying layer having brittleness in the molten aluminum plating layer as much as possible. In addition, it was confirmed that the thickness of the alloying layer is closely related to the composition of the tau phase area and the tau phase in the alloying layer.
- the alloying layer is distributed as a tau phase called a FeAl phase having a ductility on a matrix having brittleness consisting of a Fe 2 Al 5 phase.
- a soft layer is formed in the lower part of the alloying layer at the interface with the base steel sheet.
- the present inventors are important in the composition of the tau phase (the content of Si, Cr) constituting the alloying layer, and in particular, when the tau phase contains 10% or more of Si and 0.2% or more of Cr as its own weight%
- the fraction of the tau phase in the alloying layer is distributed not only to have 10% or more, but also to make the thickness of the alloying layer within 35 ⁇ m to confirm that the dropout phenomenon of the plating layer during press forming can be minimized, and the present invention is proposed. .
- the present invention finds that the fraction of the tau phase in the alloying layer and the content of Si and Cr in the tau phase affect the press formability of the plating layer.
- HPF molded member of the present invention excellent in powder resistance during press molding.
- the HPF molding member of the present invention refers to a molding member manufactured by hot forming a molten aluminum plated steel sheet in which a molten aluminum plating layer is formed on a surface of a base steel sheet.
- the base steel sheet may use a conventional cold rolled cold rolled steel sheet, it may also use a hot rolled hot rolled steel sheet.
- the base steel sheet constituting the HPF molded member of the present invention in weight%, C: 0.18 to 0.25%, Si: 0.1 to 1.0%, Mn: 0.9 to 1.5%, P: 0.03% or less, S: 0.01% or less, Al : 0.01 ⁇ 0.05%, Cr: 0.05 ⁇ 0.5%, Ti: 0.01 ⁇ 0.05%, B: 0.001 ⁇ 0.005, N: 0.009% or less, and it contains the balance Fe and other impurities.
- the steel composition of the steel sheet and the reason for limitation thereof will be described in detail below.
- C is an essential element for increasing the strength of martensite. If the C content is less than 0.18%, it is difficult to obtain sufficient strength for securing crash resistance. In addition, containing more than 0.25% may not only lower the impact toughness of the slab, but also reduce the weldability of the HPF molded member.
- the Si may not only be effective in homogenizing the material of the steel material after HPF, but also may contribute to the generation of the tau phase of the plating layer by diffusion into the plating layer during the HPF heat treatment. If the Si content is less than 0.1%, it may be difficult to achieve a sufficient effect on material uniformity and diffusion into the plating layer. If the Si content is more than 1.0%, it may be difficult to ensure good molten aluminum plating surface quality due to the Si oxide generated on the surface of the steel sheet during annealing. Since it exists, 1.0% or less is added.
- the Mn is added to secure the hardenability of the steel, such as Cr, B and the like. If the Mn content is less than 0.9%, it is difficult to secure sufficient hardenability and bainite may be produced, and thus it is difficult to secure sufficient strength. In addition, when the content exceeds 1.5%, not only the steel sheet manufacturing cost increases, but also Mn segregation in the steel material may significantly reduce the bendability of the HPF molded member. In consideration of this, in the present invention, it is preferable to limit the Mn content to 0.9 to 1.5% range.
- P is preferably added as little as possible as an element which inhibits many properties of the HPF molded member as a grain boundary segregation element. If the P content is more than 0.03%, the bending property, impact property, weldability, etc. of the molded member deteriorate, so the upper limit is preferably limited to 0.03%.
- S is preferably present as an impurity in the steel, and is added as little as possible as an element which inhibits the bending property and weldability of the molded member.
- the upper limit is preferably limited to 0.01%.
- Al is added for the purpose of deoxidation in steelmaking similarly to Si.
- Al must be added at least 0.01%, and if the content exceeds 0.05%, the effect is not only saturated but also inferior to the surface quality of the plating material, which limits the upper limit to 0.05%. It is preferable.
- the Cr is added to secure the hardenability of the steel, such as Mn, B and the like. If the Cr content is less than 0.05%, it is difficult to secure sufficient hardenability, and if the content is more than 0.5%, the hardenability is sufficiently secured, but the properties thereof may not only be saturated, but steel manufacturing costs may increase. In consideration of this, in the present invention, it is preferable to limit the content of Cr to 0.05 to 0.5% range.
- the Ti is added to remain in solid solution B essential for securing hardenability by combining with nitrogen remaining as impurities in the steel to form TiN. If the Ti content is less than 0.01%, it is difficult to fully expect the effect, and if the content is more than 0.05%, its properties may not only be saturated, but also steel manufacturing costs may increase. In consideration of this, in the present invention, it is preferable to limit the content of Ti to 0.01 ⁇ 0.05% range.
- B is added in order to secure hardenability in an HPF molded member like Mn and Cr.
- it should be added at least 0.001%, and if the content exceeds 0.005%, the effect is not only saturated but also significantly deteriorates hot rolling property. Therefore, in the present invention, it is preferable to limit the B content to 0.001% to 0.005% range.
- the N is present as an impurity in the steel and preferably added as little as possible. If the N content is more than 0.009% may cause a surface defect of the steel, it is preferable to limit the upper limit to 0.009%.
- the base steel sheet constituting the HPF molding member of the present invention more preferably further contains the following components.
- the Mo and W are hardenability and precipitation hardening elements, which are highly effective in securing high strength. If the sum of the added amounts of Mo and W is less than 0.001%, sufficient hardenability and precipitation strengthening effect may not be obtained, and if it exceeds 0.5%, the effect may not only be saturated but also the manufacturing cost may increase. Therefore, in the present invention, the content of Mo + W is preferably limited to 0.001 to 0.5% range.
- Nb, Zr, and V are elements that improve strength, refinement of grains, and heat treatment characteristics of a steel sheet.
- the content of at least one of Nb, Zr and V is less than 0.001%, it is difficult to expect such an effect, and when the content exceeds 0.4%, the manufacturing cost is excessively increased. Therefore, in the present invention, it is preferable to limit the content of these elements to 0.001 to 0.4%.
- the Cu is an element that generates fine Cu precipitates to improve the strength
- the Ni is an element effective in increasing the strength and improving the heat treatment property. If the sum of the components is less than 0.005%, the desired strength cannot be sufficiently obtained, while if the sum of the components exceeds 2.0%, it is inferior to the operability and the manufacturing cost can be increased. In consideration of this, in the present invention, it is preferable to control the Cu + Ni: 0.005 ⁇ 2.0%.
- Sb, Sn, and Bi are grain boundary segregation elements, and are concentrated at the interface between the plating layer and the base iron during HPF heating, thereby improving adhesion of the plating layer. By improving the adhesion of the plating layer, it is possible to assist in preventing the plating layer from falling off during the thermoforming. Since Sb, Sn and Bi have similar characteristics, it is also possible to mix and use three elements, At this time, it is preferable to make one or more combinations into 0.03% or less. This is because if the sum of the above components exceeds 0.03%, brittleness of the base iron may deteriorate during hot forming.
- the HPF molding member of the present invention has a molten aluminum plating layer formed on the surface of the base steel sheet having the above-described steel composition, and this plating layer is made of a soft diffusion layer and a hard alloy layer, as is known.
- the alloying layer is composed of a brittle Fe2Al5 matrix phase and a tau phase (FeAl) having ductility.
- the tau phase is formed in the boundary between the alloy layer and the diffusion layer and the alloy layer, and the tau phase formed in the alloy layer has a band shape connected to each other in a section of 50% or more in a direction perpendicular to the thickness of the plating layer. It can be achieved.
- the tau phase (FeAl) is present in the alloy layer in an area% of 10 to 30%. If the tau is less than 10% of the area ratio, the plating layer is mechanically weak, so that the plating layer may drop off during the press working, and if the tau phase exceeds 30%, weldability may be inferior.
- the tau phase is composed of 10% or more of Si and 0.2% or more of Cr (remaining components are Al and Fe) by weight.
- the composition of the tau phase as described above, not only the thickness of the alloy layer having brittleness can be controlled to be 35 ⁇ m or less, but also the area fraction of the tau phase can be controlled so that the powder-resistant powder during press molding is required in the present invention.
- the ring can provide an excellent HPF molded member.
- the tau phase is made to include Si: 10-12%, Mn + Cr: 1.3-2.0%, residual Al and Fe in its own weight%.
- the thickness ratio of the hard alloy layer / soft diffusion layer in the molten aluminum plating layer satisfies 1.5 to 3.0.
- the HPF molded member of the present invention can prevent defects such as plating layer dropout during hot forming, thereby improving powder resistance.
- the steel plate which has a steel composition component as mentioned above is provided.
- the steel sheet which has a steel composition component as mentioned above is provided.
- hot rolled steel sheet may be used as the steel sheet, but also hot rolled steel sheet may be used.
- a hot rolled steel sheet from which the scale has been removed or a cold rolled steel sheet obtained after cold rolling the hot rolled sheet may be used as the steel sheet.
- the cold rolled steel sheet may include a case in which the hot rolled steel sheet is cold rolled and then subjected to annealing heat treatment in a reducing gas atmosphere at 750 ° C. to 850 ° C.
- the composition component of the weight percent, Si 9-11%, Fe: less than 3%, balance Al and Molten aluminum plating is performed by immersing a molten aluminum plating bath including other unavoidable impurities.
- the steel sheet is charged into a heating furnace and heated, wherein the heating temperature range is preferably limited to 550 to 850 ° C. If the heating temperature of the steel sheet is less than 550 °C, the temperature difference with the plating bath is excessive, there is a fear that the plating quality is reduced by cooling the temperature of the plating bath at the time of hot dip plating, and if the temperature exceeds 850 °C deterioration of the equipment due to high temperature Because of concern.
- the steel sheet heated in the molten aluminum plating bath is maintained at 640 ⁇ 680 °C, the composition of the composition by weight, containing 9 to 11% of Si, less than 3% of Fe, the balance Al and other unavoidable impurities Is immersed in the molten aluminum plating process. If the temperature of the plating bath is less than 640 °C homogenization of the thickness of the plating layer is lowered, and if the temperature of the plating bath exceeds 680 °C may cause the port (port) of the plating bath deteriorated due to the erosion caused by the high temperature.
- the molten aluminum plating bath composition components in weight%, Si 9-11%, Fe: less than 3%, the balance Al and other unavoidable impurities are required to be composed.
- the Si content is less than 9%, not only the formation of the plating layer is uneven, but also the formation of the tau phase of the plating layer during HPF heating may be insufficient, so that the plating layer may be damaged during pressing.
- the content of Si exceeds 11% there is a problem that the temperature of the plating bath is raised to raise the plating bath management temperature.
- Fe in the plating bath is dissolved in the plating bath from the steel sheet in the plating process.
- the Fe content in the plating bath is 3% or more, the FeAl compound called dross is easily formed in the plating bath, and thus the plating quality may be impaired.
- the solidification structure is determined during the solidification process, and it is necessary to control the solidification rate because the solidification structure has an important effect on the alloying and the formation of the tau phase during the HPF heating process.
- the Al plating layer has a mixed structure of an Al phase having a hardness in the range of Hv 70-100 and a FeAlSi tertiary alloy phase having a hardness of Hv 800-1000. If the structure is non-uniform, the formation of the tau phase during the HPF heating process occurs. Since this is not sufficient or has no continuity, it is not good for suppressing plating layer embrittlement.
- the structure of the plating layer is uneven when the cooling rate until the plated layer is solidified after the hot-dip plating is within 15 °C / s, FeAlSi in addition to the Al phase in the center at the center of the plating layer if the average speed is more than 15 °C
- region in which an alloy phase does not exist is controlled uniformly within 50 micrometers on average. Locally, when the Al phase region in which the FeAlSi alloy phase is not precipitated in the center of the plating layer becomes large, intensity unevenness of the plating layer occurs.
- the length of the region in which the FeAlSi phase is deposited in the center of the plating layer is within 50 ⁇ m on average and does not exceed 100 ⁇ m at the maximum. More preferably, the average is preferably within 30 ⁇ m and not more than 50 ⁇ m at the maximum.
- the thickness of the plating layer formed by the molten aluminum plating it is preferable to control the thickness of the plating layer formed by the molten aluminum plating to be within 25 ⁇ 35 ⁇ m.
- the thickness of the plated layer is less than 25 ⁇ m, the protection of the member by the plated layer is not sufficient. If the thickness of the plated layer is 35 ⁇ m or more, the mechanical properties of the plated layer may be embrittled and powdering may occur in the plated layer.
- the molten aluminum plated steel sheet is heated to a temperature of 880 ⁇ 930 °C, and then maintained for a certain time to alloy the molten aluminum plated layer formed on the surface.
- the hot-dip galvanized steel sheet needs to be heated to at least 880 ° C or higher. It is because there exists a possibility that the austenite homogenization of a steel structure may fall when the temperature of a plated steel plate is less than 880 degreeC. On the other hand, if the temperature of the steel sheet exceeds 930 °C there is a fear of thermal degradation of the plating layer.
- the molten aluminum plating layer is alloyed. That is, a molten aluminum plating layer composed of a soft diffusion layer and a hard alloy layer can be obtained, and the alloy layer includes a brittle Fe2Al5 matrix phase and a tau phase (FeAl) having ductility.
- the tau phase (FeAl) is present in the alloy layer in an area% of 10 to 30%.
- the tau phase is preferably formed by its own weight percent, including 10% or more of Si and 0.2% or more of Cr (the remaining components are Al and Fe), and more preferably, the tau phase is in its own weight percent.
- the thickness ratio of the hard alloy layer / soft diffusion layer in the alloyed molten aluminum plating layer satisfies 1.5 to 3.0.
- the maintenance time is preferably managed not to exceed 10 minutes.
- the alloyed hot-dip steel sheet is hot formed, and at the same time, an HPF molded article is manufactured by quenching to a temperature range of 300 ° C. or less. That is, the alloyed steel sheet is molded into a press-molded mold in which the inside is water-cooled, and finishes HPF processing by removing the processing member from the mold after the temperature of the steel sheet reaches 300 ° C or lower. If the forming member is taken out of the mold at a temperature of 300 ° C or higher after hot pressing, there is a fear of deformation due to thermal stress.
- prior to hot forming the heated steel sheet by a mold may further include the step of cooling the heated steel sheet. It was confirmed that there is an effect of suppressing cracking of the plating layer during molding by the mold by preventing stress from accumulating in the plating layer through the cooling process. However, this step is only to maximize the effect of the present invention, it is not necessarily to be performed.
- the cooling rate is preferably 20 ⁇ 100 °C / s. If the cooling rate is less than 20 ° C / s, the cooling effect can not be expected, whereas, if the cooling rate exceeds 100 ° C / s, there is a fear that the martensite transformation effect due to the hot press is reduced by the supercooling.
- the cooling end temperature is preferably 700 ⁇ 780 °C. If the cooling end temperature is less than 700 ° C., there is a fear that the martensite transformation effect due to hot pressing may be reduced. On the other hand, if the cooling end temperature is higher than 780 ° C., there is a possibility that the effect of inhibiting cracking of the plating layer due to cooling may decrease.
- a cold rolled steel sheet having a thickness of 0.2mm having a composition of 0.227C-0.26Si-1.18Mn-0.014P-0.0024S-0.035Al-0.183Cr-0.034 Ti-0.0023B-0.0040N was prepared, and then the surface of the cold rolled steel sheet. Oil and contaminants were washed off.
- the cold rolled steel sheet was heated to 760 ° C., and then deposited in a plating bath maintained at 660 ° C. to form a molten aluminum plating layer on the steel sheet.
- the components other than Al in the plating bath was changed to 8-11% Si, Fe content was evaluated in the range of 1.7 ⁇ 2.5%.
- the molten aluminum plated layer was formed to cool the plated steel sheet, and the cooling rate at this time was 15 ° C / s for Inventive Example 1, Inventive Example 2, Inventive Example 3, Comparative Example 1 and Comparative Example 2, respectively, in Table 1 below. , 35 ° C / s, 45 ° C / s, 14 ° C / s and 12 ° C / s.
- the cooled plated steel sheet was charged in a heating furnace at 900 to 930 ° C. for 5 to 6 minutes as shown in Table 1 below, and HPF was continuously performed after heating. At this time, the continuous operation was performed until the defect which the debris which fell out of the plating layer on the molded member surface has more than 0.5 mm in width, and the number becomes five or more.
- Table 1 shows the plating bath composition and plating layer thickness used in the manufacture of the plated steel sheet used in the press formability evaluation, the fraction of the tau phase after heat treatment, the composition thickness, and the like, and summarizes the number of times that continuous operation is possible. .
- the absolute value of the number of continuous operations may vary depending on the shape and material of the mold, it can be seen that in the present embodiment, the number of continuous operations increases and decreases significantly according to the structure and composition of the alloy layer.
- the fraction of the tau phase means the fraction of the tau phase in the alloy layer, and the composition of the tau phase means its own weight% (residual Fe).
- the thickness of the alloy layer was all 35 ⁇ m or less, In addition, it can be seen that the number of continuous operation is also excellent as more than 255.
- FIG. 1 is a photograph showing a plated layer cross section of Inventive Example 1.
- FIG. 1 shows that after the HPF processing, the plating layer is composed of an alloy layer and a diffusion layer, it can be seen that the tau phase appears as a dark color in the alloy layer.
- Comparative Example 1-2 containing less than 10% of Si in the composition of the tau phase constituting the alloy layer, the alloy layer thickness was more than 35 ⁇ m, and the number of continuous operations was also poor, which was not more than 85.
- Can be. 2 is a structure photograph showing a cross section of a plating layer of Comparative Example 1.
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Abstract
Description
구분 | 도금욕 조성(wt%) | 가열온도(℃) | 가열시간(min) | 타우상 분율(%) | 타우상의 조성(wt%) | 합금층 두께(㎛) | 합금층/확산층) 비 | 연속조업횟수 | |||||
Al | Si | Fe | Al | Si | Cr | Mn | |||||||
발명예1 | 88.5 | 9.7 | 1.8 | 900 | 5 | 21 | 22.6 | 10.29 | 0.28 | 1.3 | 30.5 | 2.8 | 255 |
발명예2 | 88.5 | 9.7 | 1.8 | 930 | 6 | 27 | 23.5 | 10.50 | 0.23 | 1.4 | 30.2 | 1.75 | 290 |
발명예3 | 87.0 | 11 | 2.0 | 900 | 6 | 19 | 21.1 | 11.5 | 0.25 | 1.2 | 29.4 | 2.2 | 260 |
비교예1 | 89.1 | 8.8 | 2.0 | 900 | 6 | 7.2 | 28.5 | 8.34 | 0.15 | 1.1 | 36 | 9.5 | 80 |
비교예2 | 89.5 | 8.0 | 2.5 | 900 | 6 | 5.9 | 29.5 | 8.11 | 0.18 | 1.0 | 37 | 8.2 | 85 |
Claims (25)
- 소지 강판의 표면에 Al을 포함하는 용융도금층이 형성되어 있는 HPF 성형 부재에 있어서, 상기 소지강판은, 중량%로 C : 0.18~0.25%, Si : 0.1~1.0%, Mn : 0.9~1.5%, P : 0.03% 이하, S : 0.01%이하, Al : 0.01~0.05%, Cr : 0.05~0.5%, Ti : 0.01~0.05%, B : 0.001~0.005 , N : 0.009%이하, 잔부 Fe 및 기타 불순물로 포함하고;상기 용융도금층은 연질의 확산층과 경질의 합금층으로 이루어지고;상기 합금층에는 타우상이 면적%로 10~30% 범위로 존재하고 있으며; 그리고상기 합금층은 그 두께가 35㎛ 이하가 되도록, 상기 타우상이 자체 중량%로, Si을 10% 이상, Cr을 0.2% 이상 포함하여 조성됨을 특징으로 프레스성형시 내파우더링이 우수한 HPF 성형 부재.
- 제 1항에 있어서, 상기 소지강판은 냉연강판 또는 열연강판인 것을 특징으로 하는 프레스 성형시 내파우더링이 우수한 HPF 성형 부재.
- 제 1항에 있어서, 상기 타우상은 자체 중량%로 Si:10~12%, Mn+Cr:1.3~2.0 %, 잔여 Fe 및 Al을 포함하여 조성됨을 특징으로 하는 프레스 성형시 내파우더링이 우수한 HPF 성형 부재.
- 제 1항에 있어서, 상기 용융도금층에서 합금층/확산층의 두께비가 1.5~3.0를 만족함을 특징으로 하는 프레스성형시 내파우더링이 우수한 HPF 성형 부재.
- 제 1항에 있어서, 상기 타우상은 상기 합금층과 확산층의 경계 및 상기 합금층 내부에 형성되며, 상기 합금층 내부에 형성되는 타우상은 도금층 두께에 수직 방향으로 50% 이상의 구간에서 서로 연결된 띠 형태를 이루고 있음을 특징으로 하는 프레스성형시 내파우더링이 우수한 HPF 성형 부재.
- 제 1항에 있어서, 상기 소지강판은 Mo + W : 0.001~0.5%로 추가로 포함함을 특징으로 하는 프레스성형시 내파우더링이 우수한 HPF 성형 부재.
- 제 1항에 있어서, 상기 소지강판은 Nb, Zr 또는 V 중 1종 이상의 합: 0.001~0.4% 범위로 추가로 포함함을 특징으로 하는 프레스성형시 내파우더링이 우수한 HPF 성형 부재.
- 제 1항에 있어서, 상기 소지강판은 Cu + Ni: 0.005~2.0% 범위로 추가로 포함함을 특징으로 하는 프레스성형시 내파우더링이 우수한 HPF 성형 부재.
- 제 1항에 있어서, 상기 소지강판은 Sb, Sn 또는 Bi 중 1종 이상을 0.03% 이하로 추가로 포함함을 특징으로 하는 프레스성형시 내파우더링이 우수한 HPF 성형 부재.
- 중량%로 C : 0.18~0.25%, Si : 0.1~1.0%, Mn : 0.9~1.5%, P : 0.03% 이하, S : 0.01%이하, Al : 0.01~0.05%, Cr : 0.05~0.5%, Ti : 0.01~0.05%, B : 0.001~0.005 , N : 0.009%이하, 잔부 Fe 및 기타 불순물을 포함하는 강판을 마련하는 공정;상기 강판을 550~850℃의 온도로 가열한 후, 640~680℃로 유지되고, 그 조성성분이 중량%로, Si 9~11%, Fe:3% 미만, 잔부 Al 및 기타 불가피한 불순물을 포함하여 조성되는 용융알루미늄 도금욕에 침지하여 용융알루미늄 도금처리하는 공정;상기 용융알루미늄 도금강판을 880~930℃의 온도로 가열한 후, 일정시간 유지함으로써 그 표면의 용융알루미늄 도금층을 합금화시키는 공정; 및상기 합금화된 용융알루미늄 도금강판을 열간성형함과 동시에, 300℃이하의 온도범위까지 급냉시킴으로써 HPF 성형품을 제조하는 공정;을 포함하는 프레스성형시 내파우더링이 우수한 HPF 성형 부재의 제조방법.
- 제 10항에 있어서, 상기 합금화된 용융알루미늄 도금층은 연질의 확산층과 경질의 합금층으로 이루어지고; 상기 합금층에는 타우상이 면적%로 10~30% 범위로 존재하고 있으며; 그리고 상기 타우상이 자체 중량%로, Si을 10% 이상, Cr을 0.2% 이상 포함하여 조성되어 있음을 특징으로 하는 프레스성형시 내파우더링이 우수한 HPF 성형 부재의 제조방법.
- 제 11항에 있어서, 상기 타우상은 자체 중량%로 Si:10~12%, Mn+Cr:1.3~2.0 %, 잔여 Fe 및 Al을 포함하여 조성됨을 특징으로 하는 프레스성형시 내파우더링이 우수한 HPF 성형 부재의 제조방법.
- 제 11항에 있어서, 상기 합금화 용융알루미늄 도금층에서 합금층/확산층의 두께비가 1.5~3.0를 만족함을 특징으로 하는 프레스성형시 내파우더링이 우수한 HPF 성형 부재의 제조방법.
- 제 10항에 있어서, 상기 강판은 냉연강판 또는 열연강판인 것을 특징으로 하는 프레스성형시 내파우더링이 우수한 HPF 성형 부재의 제조방법.
- 제 10항에 있어서, 상기 용융알루미늄 도금 후, 도금층이 응고될 때까지의 15℃/s 이상의 평균 냉각속도로 냉각함을 특징으로 하는 프레스성형시 내파우더링이 우수한 HPF 성형 부재의 제조방법.
- 제 10항에 있어서, 상기 합금화된 용융알루미늄 도금강판을 열간성형에 앞서, 700~780℃의 온도 범위까지 20~100℃/s의 냉각속도로 냉각하는 공정;을 추가로 포함하는 프레스성형시 내파우더링이 우수한 HPF 성형 부재의 제조방법.
- 제 10항에 있어서, 상기 강판은 Mo + W : 0.001~0.5%로 추가로 포함함을 특징으로 하는 프레스성형시 내파우더링이 우수한 HPF 성형 부재의 제조방법.
- 제 10항에 있어서, 상기 강판은 Nb, Zr 또는 V 중 1종 이상의 합: 0.001~0.4% 범위로 추가로 포함함을 특징으로 하는 프레스성형시 내파우더링이 우수한 HPF 성형 부재의 제조방법.
- 제 10항에 있어서, 상기 강판은 Cu + Ni: 0.005~2.0% 범위로 추가로 포함함을 특징으로 하는 프레스성형시 내파우더링이 우수한 HPF 성형 부재의 제조방법.
- 제 10항에 있어서, 상기 강판은 Sb, Sn 또는 Bi 중 1종 이상을 0.03% 이하로 추가로 포함함을 특징으로 하는 프레스성형시 내파우더링이 우수한 HPF 성형 부재의 제조방법.
- 중량%로 C : 0.18~0.25%, Si : 0.1~1.0%, Mn : 0.9~1.5%, P : 0.03% 이하, S : 0.01%이하, Al : 0.01~0.05%, Cr : 0.05~0.5%, Ti : 0.01~0.05%, B : 0.001~0.005 , N : 0.009%이하, 잔부 Fe 및 기타 불순물을 포함하는 소지강판 표면에 용융알루미늄 도금층이 형성된 용융알루미늄 도금강판을 마련하는 공정;상기 용융알루미늄 도금강판을 880~930℃의 온도로 가열한 후, 일정시간 유지함으로써 그 표면의 용융알루미늄 도금층을 합금화시키는 공정; 및상기 합금화된 용융알루미늄 도금강판을 열간성형함과 동시에, 300℃이하의 온도범위까지 급냉시킴으로써 HPF 성형품을 제조하는 공정;을 포함하는 프레스 성형시 내파우더링이 우수한 HPF 성형 부재의 제조방법.
- 제 21항에 있어서, 상기 합금화된 용융알루미늄 도금층은 연질의 확산층과 경질의 합금층으로 이루어지고; 상기 합금층에는 타우상이 면적%로 10~30% 범위로 존재하고 있으며; 그리고 상기 합금층은 그 두께가 35㎛ 이하가 되도록, 상기 타우상이 자체 중량%로, Si을 10% 이상, Cr을 0.2% 이상 포함하여 조성되어 있음을 특징으로 하는 프레스 성형시 내파우더링이 우수한 HPF 성형 부재의 제조방법.
- 제 21항에 있어서, 상기 소지강판은 냉연강판 또는 열연강판인 것을 특징으로 하는 프레스 성형시 내파우더링이 우수한 HPF 성형 부재의 제조방법.
- 제 22항에 있어서, 상기 타우상은 자체 중량%로 Si:10~12%, Mn+Cr:1.3~2.0 %, 잔여 Fe 및 Al을 포함하여 조성됨을 특징으로 하는 프레스 성형시 내파우더링이 우수한 HPF 성형 부재의 제조방법.
- 제 22항에 있어서, 상기 용융알루미늄 도금층에서 합금층/확산층의 두께비가 1.5~3.0를 만족함을 특징으로 하는 프레스 성형시 내파우더링이 우수한 HPF 성형 부재의 제조방법.
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CN114761602B (zh) * | 2019-12-20 | 2023-06-20 | Posco公司 | 加工性和耐蚀性优异的铝基合金镀覆钢板及其制造方法 |
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CN106164317A (zh) | 2016-11-23 |
US20180223387A1 (en) | 2018-08-09 |
US20160362764A1 (en) | 2016-12-15 |
EP3239336A1 (en) | 2017-11-01 |
WO2016104879A8 (ko) | 2016-09-29 |
US10808292B2 (en) | 2020-10-20 |
JP6437635B2 (ja) | 2018-12-12 |
US9963758B2 (en) | 2018-05-08 |
ES2875073T3 (es) | 2021-11-08 |
JP2017535666A (ja) | 2017-11-30 |
KR101569509B1 (ko) | 2015-11-17 |
MX2017003310A (es) | 2017-06-23 |
CN106164317B (zh) | 2018-08-07 |
CN108893694A (zh) | 2018-11-27 |
EP3239336A4 (en) | 2017-11-01 |
EP3239336B1 (en) | 2021-03-17 |
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