CN115109967B - Hot dip high-strength steel plate and preparation method thereof - Google Patents
Hot dip high-strength steel plate and preparation method thereof Download PDFInfo
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- CN115109967B CN115109967B CN202210715613.8A CN202210715613A CN115109967B CN 115109967 B CN115109967 B CN 115109967B CN 202210715613 A CN202210715613 A CN 202210715613A CN 115109967 B CN115109967 B CN 115109967B
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C18/00—Alloys based on zinc
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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
- C21D1/26—Methods of annealing
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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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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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
- C21D8/0226—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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- 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
- C21D8/0242—Flattening; Dressing; Flexing
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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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
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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
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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
- 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
- C23C2/26—After-treatment
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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
- C23C2/26—After-treatment
- C23C2/28—Thermal after-treatment, e.g. treatment in oil bath
Abstract
The application particularly relates to a hot dip high-strength steel plate and a preparation method thereof, and belongs to the technical field of steel preparation. The hot dip high-strength steel plate comprises a substrate and a plating layer on the surface of the substrate, wherein the plating layer comprises the following chemical components in percentage by mass; al:5-15%, si:2-5%, ni:10-20%, and the balance of Zn and unavoidable impurities. According to the method, al, si and Ni elements are added into a coating, high-temperature compounds with the melting point temperature exceeding 1000 ℃ are formed in the coating, and the compounds can be kept in a solid state in liquid metal during welding, so that the melting point of the coating can be improved, the surface energy of the molten coating can be improved, the wettability between the coating and a steel matrix is reduced, the contact area between the molten liquid metal of the coating and a steel plate is kept small, the brittleness sensitivity of the liquid metal is reduced, and the situation that cracks appear at the grain boundary positions due to the fact that the coating is easy to melt and infiltrate into the grain boundary of the surface layer of a substrate in the welding process is improved.
Description
Technical Field
The application belongs to the technical field of steel preparation, and particularly relates to a hot dip high-strength steel plate and a preparation method thereof.
Background
The continuous hot dip galvanized high strength steel is an important raw material for producing automobile bodies. Compared with the traditional steel plate, the high-strength steel can obviously reduce the thickness of the steel plate on the premise of not weakening the safety performance, thereby realizing light weight. However, steel sheets have poor corrosion resistance in the atmosphere and thus often require special treatment, and hot dip galvanization is a common method for improving the corrosion resistance of steel sheets. The hot dip galvanized high strength steel is used, so that on one hand, the weight reduction can be realized, and on the other hand, the corrosion life can be prolonged.
However, the conventional continuous hot dip galvanized high strength steel has a certain application difficulty, wherein one of the problems is that the hot dip galvanized high strength steel is easy to generate surface cracks of the steel plate in the welding process of the vehicle body. In the welding process, the temperature near the welding point often exceeds the melting point temperature of the galvanized layer, so that the galvanized layer is partially melted, and meanwhile, the microstructure of the high-strength steel is completely changed into austenite due to the local high temperature of welding, so that the strength is obviously reduced. The melted zinc is easily diffused along the grain boundary of austenite on the surface of the steel sheet, resulting in grain boundary brittleness of the austenite. When the steel sheet cools down, austenite reconverts to ferrite or martensite, and the grain boundaries undergo a large stress concentration, resulting in cracks at the grain boundary positions, which are generally called liquid metal induced cracks, and the tendency of high-strength steel to crack at high temperature welding is called liquid metal brittleness.
Disclosure of Invention
The application aims to provide a hot dip high-strength steel plate and a preparation method thereof, which are used for solving the technical problem that the hot dip high-strength steel plate in the prior art is high in liquid metal brittleness.
The embodiment of the application provides a hot dip high-strength steel plate, which comprises a substrate and a coating on the surface of the substrate, wherein the chemical components of the coating comprise the following components in percentage by mass;
al:5-15%, si:2-5%, ni:10-20%, and the balance of Zn and unavoidable impurities.
Optionally, a bonding layer is formed between the substrate and the plating layer, and the bonding layer includes a Ni-Si compound and a Fe-Al-Ni compound;
the sum of the volume percentages of the Ni-Si compound and the Fe-Al-Ni compound of the bonding layer is more than or equal to 90 percent;
the sum of the volume percentages of the Ni-Si compound and the Fe-Al-Ni compound at the joint of the bonding layer and the plating layer is 1-10%.
Optionally, the chemical composition of the substrate includes: mn, si and B, wherein the chemical components of the substrate in mass percent satisfy the following conditions:
Mn+2Si+100B≤2.5％；
Mn+2Si+100B≥1.5％。
optionally, the chemical components of the substrate further include, in mass percent:
Cu：0.1-1.0％，S：0.005-0.010％。
optionally, the austenite volume fraction of the substrate is less than or equal to 20% at 800 ℃.
Based on the same inventive concept, the embodiment of the application also provides a preparation method of the hot dip plated high strength steel plate, which comprises the following steps:
obtaining a substrate slab with the chemical composition identical to that of the substrate;
heating, rough rolling, finish rolling, cooling, coiling, cold rolling and continuous annealing are carried out on the substrate plate blank to obtain an annealed substrate;
carrying out hot galvanizing, heat treatment and finishing on the annealed substrate to obtain the hot dip high-strength steel plate;
wherein:
the chemical composition of the hot galvanizing plating solution is the same as that of the plating layer.
Optionally, the end point temperature of the heating is 1100-1200 ℃.
Optionally, the dew point temperature of the continuous annealing is-40 to 20 ℃.
Optionally, the temperature of the annealing substrate is 400-450 ℃ when the hot galvanizing is performed.
Optionally, the temperature of the heat treatment is 450-550 ℃, and the time of the heat treatment is 10-20s.
One or more technical solutions in the embodiments of the present application at least have the following technical effects or advantages:
according to the hot dip high-strength steel plate provided by the embodiment of the application, the Al, si and Ni elements are added into the coating, so that high-temperature compounds with the melting point temperature exceeding 1000 ℃ such as Ni-Si, ni-Al and Fe-Al-Ni are formed in the coating, and can be kept in a solid state in liquid metal during welding, so that the melting point of the coating can be improved on one hand, the surface energy of the molten coating can be improved on the other hand, the wettability between the coating and a steel matrix can be reduced, the contact area between the molten liquid metal of the coating and the steel plate can be kept small, the brittleness sensitivity of the liquid metal can be reduced, the liquid metal is difficult to spread on the whole substrate surface, the possibility that the liquid metal permeates into fine grain boundaries can be reduced, the situation that the coating is easy to melt and infiltrate into the surface layer of the substrate to cause cracks at the grain boundary positions in the welding process can be improved, and the hot dip high-strength steel plate has lower brittleness of the liquid metal.
The foregoing description is only an overview of the present application, and is intended to be implemented in accordance with the teachings of the present application in order that the same may be more clearly understood and to make the same and other objects, features and advantages of the present application more readily apparent.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present application, the drawings required for the description of the embodiments will be briefly described below, and it is obvious that the drawings in the following description are some embodiments of the present application, and other drawings may be obtained according to these drawings without inventive effort for a person skilled in the art.
Fig. 1 is a flow chart of a method provided by an embodiment of the present application.
Detailed Description
The advantages and various effects of the present application will be more clearly apparent from the following detailed description and examples. It will be understood by those skilled in the art that these specific embodiments and examples are intended to illustrate the application, not to limit the application.
Throughout the specification, unless specifically indicated otherwise, the terms used herein should be understood as meaning as commonly used in the art. Accordingly, unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this application belongs. In case of conflict, the present specification will control. The terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting of the scope of the present application. For example, room temperature may refer to a temperature in the range of 10 to 35 ℃.
Unless otherwise specifically indicated, the various raw materials, reagents, instruments, equipment and the like used in the present application are commercially available or may be prepared by existing methods.
The technical scheme of the embodiment of the application aims to solve the technical problems, and the overall thought is as follows:
according to an exemplary embodiment of the application, there is provided a hot dip plated high strength steel sheet, including a substrate and a plating layer on a surface of the substrate, wherein chemical components of the plating layer include, in mass percent;
al:5-15%, si:2-5%, ni:10-20%, and the balance of Zn and unavoidable impurities.
In the welding process of the hot dip high-strength steel plate, the plating layer is melted to form liquid metal, and if a good wetting relation is formed between the liquid metal and the steel plate, the liquid metal can be easily spread on the surface of the whole substrate, so that the liquid metal can be easily infiltrated into fine grain boundaries. Therefore, if the wettability of the liquid metal on the surface of the steel plate is poor, the contact area between the liquid metal and the steel plate can be kept small, so that the brittleness sensitivity of the liquid metal is reduced. In order to achieve the object, the present application adds a large amount of Al, si, ni elements to the plating layer. The addition of these elements can form high temperature compounds such as Ni-Si, ni-Al, fe-Al-Ni with melting point temperature exceeding 1000 ℃ in the coating, which can keep solid state in liquid metal during welding, thereby improving the surface energy of the melted coating and reducing the wettability between the coating and the steel matrix, and the specific mechanism is as follows.
The main chemical elements and the limiting range are described in detail as follows:
ni: on the one hand, the melting point temperature of the zinc alloy coating can be increased to more than 500 ℃ by adding 10-20% of Ni into the coating, and the liquid metal formed in the welding process is obviously reduced. On the other hand, the corrosion resistance of the plating layer can be improved, because Ni can form a surface passivation layer in the atmosphere in Zn, and the cathode reaction of surface electrochemistry is delayed.
Si: in order to obtain enough high temperature compound, 2-5% of Si element is added simultaneously, si can form high temperature compound Ni with Ni 3 Si and Ni 2 The melting point temperature of the Si and the two compounds exceeds 800 ℃ and exceeds the surface temperature in the traditional welding, so that the melting point of the coating can be obviously improved; if the Si content is too low, ni having a sufficiently high melting point cannot be formed 3 Si and Ni with high melting point 2 Si; if the Si element content is too high, coarse Ni tends to be formed 3 Si and Ni 2 Si, leading to Ni 3 Si and Ni 2 Si is discontinuously distributed in the coating, so that the effect of preventing liquid metal zinc from penetrating into the surface of the substrate cannot be achieved, and cracks appear at the grain boundary position; on the other hand, too high a Si content also reduces the corrosion resistance of the plating layer.
Al: when Al element is added into the coating, the Al element tends to chemically react with the substrate to form Fe-Al compound which is adhered to the surface of the steel plate to form a bonding layer between the coating and the steel plate, and the compound has higher melting point and good toughness, improves the bonding force between the coating and the steel plate while improving the melting point of the coating, and simultaneously improves the corrosion resistance at high temperature.
In addition, si can inhibit the overquick growth of the Fe-Al compound layer to form a compact compound layer, so that the capability of preventing liquid metal zinc from penetrating into the surface of the substrate is further improved; the addition of Ni element can form Fe-Al-Ni ternary compound, and the melting point temperature of the ternary compound exceeds 1000 ℃, so that the melting point of the plating layer can be further improved. The content of Al element is an important guarantee for forming Fe-Al and other compounds, and therefore, the content cannot be lower than 5%; however, too much addition of the Al element causes a remarkably coarse Al-rich initial solidification structure in the plating layer, which has a deteriorated effect on corrosion resistance, and too much addition of the Al element causes too coarse Fe-Al, fe-Al-Ni, etc. compounds and also causes a volume fraction of Fe-Al-Ni compounds to be too large, thereby failing to form a dense and continuous bonding layer, and also causing a reduction in high temperature phase ratio in the bonding layer, which is disadvantageous in terms of lowering liquid metal brittleness, and also severely deteriorates corrosion resistance of the plating layer, and also deteriorates adhesion of the plating layer. Therefore, it is preferable that the content of Al element is not more than 15%.
Al and Zn can also form Zn-Al solid solution, so that the stability of the coating under the atmospheric corrosion condition is improved.
As an alternative embodiment, a bonding layer is formed between the substrate and the plating layer, the bonding layer including a Ni-Si compound and a Fe-Al-Ni compound; the sum of the volume percentages of the Ni-Si compound and the Fe-Al-Ni compound of the bonding layer is more than or equal to 90 percent; the sum of the volume percentages of the Ni-Si compound and the Fe-Al-Ni compound at the joint of the bonding layer and the plating layer is 1-10%.
The reason for controlling the above parameter ranges is that: the Ni-Si compound formed in the plating layer is dispersed in the plating layer, and the Fe-Al-Ni compound is mainly formed on the surface of the steel sheet, forming a main part of the bonding layer. In order to ensure that the high-strength steel cannot be greatly infiltrated into the grain boundary of the steel plate after the coating is melted in the welding process, the bonding layer is required to have good high-temperature stability, so that the sum of the volume fractions of the high-temperature phase Ni-Si compound and the Fe-Al-Ni compound in the bonding layer is required to be more than or equal to 90%. In addition, the volume fraction of the high-temperature compound Ni-Si compound and the Fe-Al-Ni compound in the coating is generally not less than 1%, so that the coating is not easy to form large-area molten metal in the high-temperature welding process; however, if the volume fraction of these compounds exceeds 10%, the corrosion resistance of the plating layer is seriously deteriorated, and at the same time the adhesion of the plating layer is also deteriorated, so that the sum of the volume percentages of the Ni-Si compound and the Fe-Al-Ni compound at the junction of the junction layer and the plating layer is controlled to be 1 to 10%.
As an alternative embodiment, the chemical composition of the substrate includes: mn, si and B, wherein the chemical components of the substrate in mass percent satisfy the following conditions: mn+2Si+100B is less than or equal to 2.5%; mn+2Si+100B is more than or equal to 1.5 percent.
The reason for controlling the above conditions is that: if oxides are formed on the surface of the steel sheet, wettability between the molten plated metal and the steel sheet can be reduced from the other hand. Therefore, si, mn and B are added into the substrate, oxide enrichment is easily formed on the surface of the substrate during the annealing process of the substrate, and Mn+2Si+100B is required to be more than or equal to 1.5 percent for better oxide enrichment, but if too much is added, surface oxide is caused to form a continuous and compact film, the reaction between the plating solution and the steel plate during the hot dip plating process is hindered, and the adhesiveness and corrosion resistance of the plating layer are reduced, so that Mn+2Si+100B is required to be less than or equal to 2.5 percent.
As an alternative embodiment, the chemical components of the substrate further include, in mass percent: cu:0.1-1.0%, S:0.005-0.010%.
The reason why the above elements are added and the range is controlled is that: cu and S can form Cu during hot rolling and continuous annealing 2 S fine precipitate, which is gathered to grain boundary position, can improve strength of austenite grain boundary, and Cu 2 The S fine precipitate can also react with infiltrated Zn to form Cu-Zn high-temperature solid solution to prevent further diffusion of liquid zinc, so as to achieve the aimThe substrate needs to be added with 0.1-1.0% of Cu and 0.005-0.01% of S, but if the content is too high, cu can cause brittleness of the material at high temperature, S can cause brittleness of the material at low temperature, both the brittleness of the grain boundary can be increased, the brittleness of liquid metal is increased, and if the content is too low, enough precipitate cannot be formed to be enriched to the grain boundary position, so that the optimization effect cannot be achieved.
As an alternative embodiment, the substrate has an austenite volume fraction of 20% or less at 800 ℃.
The reason for controlling the above conditions is that: the high-strength steel can form a large amount of high-temperature austenite phase due to higher local temperature in the welding process, and the high-temperature austenite phase can form low-temperature ferrite phase in the solidification cooling process. Because of the apparent density difference between austenite and ferrite, strong stress concentrations are generated inside, and the stress concentrations can cause cracking at the grain boundary positions locally infiltrated into the liquid metal. Therefore, the austenite volume fraction at 800 ℃ in the high-strength steel is required to be not more than 20%.
According to another exemplary embodiment of the present application, there is provided a method for manufacturing the hot dip plated high strength steel sheet as provided above, comprising the steps of:
s1, obtaining a substrate slab with the chemical composition identical to that of the substrate.
And S2, heating, rough rolling, finish rolling, cooling, coiling, cold rolling and continuous annealing the substrate plate blank to obtain an annealed substrate.
And S3, carrying out hot galvanizing, heat treatment and finishing on the annealed substrate to obtain the hot dip plated high-strength steel plate.
Wherein: the chemical composition of the hot galvanizing plating solution is the same as that of the plating layer.
As an alternative embodiment, the end point temperature of the heating is 1100-1200 ℃.
The reason for controlling the end point temperature of heating is that: during the heating of the base plate slab, the alloying elements dissolve into the austenite, if the slab heating temperature is too high, cu can be caused in the subsequent rough rolling and finish rolling processesIs difficult to precipitate rapidly, so that coarse precipitates are formed and are difficult to be adsorbed by grain boundaries, therefore, the heating temperature of a slab cannot exceed 1200 ℃, and if the heating temperature is too low, cu compound Cu in the rough rolling process is caused 2 S precipitates rapidly, causing rolling cracks, and therefore, the slab heating temperature cannot be lower than 1100 ℃.
As an alternative embodiment, the dew point temperature of the continuous annealing is from-40 ℃ to 20 ℃.
The reason for controlling the dew point temperature of the continuous annealing is that: in the welding process of the hot dip coating high-strength steel, the coating is melted to form liquid metal, if a good wetting relation is formed between the liquid metal and the base plate, the liquid metal is easy to spread on the whole surface of the steel plate and then is easier to infiltrate into fine grain boundaries, so that if the wetting property of the liquid metal on the surface of the steel plate is poor, the liquid metal and the steel plate can be kept at a small contact area, and the brittleness sensitivity of the liquid metal is reduced. In order to achieve the purpose, the dew point temperature of the continuous annealing process needs to be controlled, so that partial oxide is formed on the surface of the high-strength steel, the dew point temperature is too high, the oxide is too much formed, the reaction between the plating solution and the steel plate in the hot dip plating process is hindered, the adhesiveness and corrosion resistance of the plating layer are reduced, and the oxide cannot be formed if the dew point temperature is too low. It is therefore desirable that the dew point temperature be between-40 ℃ and-20 ℃.
As an alternative embodiment, the temperature of the annealing substrate is 400-450 ℃ when the hot dip galvanizing is performed.
The reason for controlling the above conditions is that: when the annealed substrate is hot galvanized, the surface temperature of the annealed substrate is an important energy source of a bonding layer between a plating layer and a steel plate, the surface temperature of the steel plate is low, the zinc liquid reacts slowly on the surface of the steel plate, the Al element in the plating layer is not fast enough to form Fe-Al-Ni compounds with the steel plate, or the formed Fe-Al-Ni compounds are not dense to form the bonding layer, so that the content of Fe-Al-Ni and Ni-Si compounds in the bonding layer is small, if the surface temperature of the steel plate is too high, the steel plate fast reacts with Al, si, ni and the like in the zinc liquid to form coarse Fe-Al-Ni and Ni-Si compounds, the bonding layer is loose, and more Zn is permeated into the bonding layer, so that the content of Fe-Al-Ni and Ni-Si compounds in the bonding layer is small, and the temperature of the annealed substrate is 400-450 ℃.
As an alternative embodiment, the temperature of the heat treatment is 450-550 ℃, and the time of the heat treatment is 10-20s.
The reason for controlling the above conditions is that: the purpose of the heat treatment is to further collect Fe-Al-Ni compounds in the coating to the surface of the steel plate to form a complete bonding layer, and at the same time, the heat treatment process can further induce Cu 2 S precipitates are gathered at the grain boundary position, the heat treatment temperature cannot be too high, the heat treatment time cannot be too long, otherwise the mechanical property of the high-strength steel plate is seriously influenced, the corrosion resistance of a coating is adversely affected, and Cu is caused 2 S precipitate is coarsened excessively, the effect of strengthening grain boundary is not achieved, the beneficial effect is weakened, and meanwhile, the temperature of heat treatment cannot be too low, otherwise, the purpose is not achieved, so that the temperature of heat treatment is controlled to be 450-550 ℃, and the time of heat treatment is controlled to be 10-20S.
The present application will be described in detail with reference to examples, comparative examples and experimental data.
Examples 1 to 7
A hot dip high strength steel plate is provided, which comprises a substrate and a coating on the surface of the substrate, and various parameters are shown in Table 1.
Table 1 parameters of hot dip plated high strength steel sheet of examples 1 to 7
The preparation method of the hot dip plated high strength steel plate comprises the following steps:
s1, obtaining a substrate slab with the chemical composition identical to that of the substrate.
And S2, heating, rough rolling, finish rolling, cooling, coiling, cold rolling and continuous annealing the substrate plate blank to obtain an annealed substrate.
And S3, carrying out hot galvanizing, heat treatment and finishing on the annealed substrate to obtain the hot dip plated high-strength steel plate.
The parameters of the preparation method of each example are shown in Table 2.
TABLE 2 parameters of the preparation methods of examples 1-7
Comparative examples 1 to 5
A hot dip high strength steel sheet is provided, comprising a substrate and a coating layer on the surface of the substrate, and the parameters are shown in Table 3.
Table 3 parameters of hot dip plated high strength steel sheet of comparative examples 1 to 5
The preparation method of the hot dip plated high strength steel sheet was the same as that of examples 1 to 7, and the parameters of the preparation methods of the respective comparative examples are shown in Table 4, respectively.
TABLE 4 parameters of the preparation methods of comparative examples 1 to 5
Experimental example
The hot dip plated high strength steel sheets provided in examples 1 to 7 and comparative examples 1 to 5 were evaluated for liquid metal brittleness, plating adhesion, and corrosion resistance, respectively.
The operation method comprises the following steps: bending the hot dip high strength steel plate by 180 degrees, wherein the bending radius is the same as the thickness of the steel plate, and then observing whether the plating layer at the outer edge of the bending is peeled off or not. If peeling occurs, the adhesion is failed, marked as x, and if peeling does not occur, the adhesion is accepted, marked as o. The hot dip galvanized high strength steel is heated to 1000 ℃ at a speed of 20K/s, kept for 20 seconds, subjected to tensile deformation for 20 seconds during the heat preservation, subjected to deformation speed of 10/s, and then rapidly cooled to room temperature. And observing and measuring cracks appearing on the surface layer of the high-strength steel plate, measuring the density of the cracks, and measuring the maximum depth of the cracks, wherein the deeper the crack depth is, the greater the crack density is, which shows that the brittleness of the liquid metal is more obvious. The corrosion resistance of the material was evaluated by using a neutral salt spray test for 500 hours, and the thickness reduction of the plating layer before and after the test was measured. The thickness of the coating is reduced and thinned, which indicates that the corrosion resistance is poorer. The evaluation results are shown in the following table:
as can be seen from the above table, the hot dip plated high strength steel sheet according to examples 1 to 7 of the present application is significantly superior to comparative examples 1 to 5 in terms of liquid metal brittleness, plating adhesion and corrosion resistance.
Finally, it is also noted that the terms "comprises," "comprising," or any other variation thereof, are intended to cover a non-exclusive inclusion, such that a process, method, article, or apparatus that comprises a list of elements does not include only those elements but may include other elements not expressly listed or inherent to such process, method, article, or apparatus.
While preferred embodiments of the present application have been described, additional variations and modifications in those embodiments may occur to those skilled in the art once they learn of the basic inventive concepts. It is therefore intended that the following claims be interpreted as including the preferred embodiments and all such alterations and modifications as fall within the scope of the application.
It will be apparent to those skilled in the art that various modifications and variations can be made to the present application without departing from the spirit or scope of the application. Thus, it is intended that the present application also include such modifications and alterations insofar as they come within the scope of the appended claims or the equivalents thereof.
Claims (6)
1. The hot dip high-strength steel plate is characterized by comprising a substrate and a coating on the surface of the substrate, wherein the coating comprises the following chemical components in percentage by mass;
al:5-15%, si:2-5%, ni:10-20%, and the balance of Zn and unavoidable impurities;
a bonding layer is formed between the substrate and the plating layer, and the bonding layer comprises a Ni-Si compound and a Fe-Al-Ni compound;
the sum of the volume percentages of the Ni-Si compound and the Fe-Al-Ni compound of the bonding layer is more than or equal to 90 percent;
the sum of the volume percentages of the Ni-Si compound and the Fe-Al-Ni compound at the joint of the bonding layer and the plating layer is 1-10%;
the chemical components of the substrate comprise: mn, si and B, wherein the chemical components of the substrate in mass percent satisfy the following conditions:
Mn+2Si+100B≤2.5%；
Mn+2Si+100B≥1.5%；
the preparation method of the hot dip high-strength steel plate comprises the steps of heating a base plate blank, rough rolling, finish rolling, cooling, coiling, cold rolling and continuous annealing to obtain an annealed base plate; and hot galvanizing the annealing substrate, wherein the dew point temperature of continuous annealing is between-40 ℃ and-20 ℃, and the temperature of the annealing substrate is between 400 ℃ and 450 ℃ when hot galvanizing is performed.
2. The hot-dip plated high strength steel sheet according to claim 1, wherein the chemical composition of the substrate further comprises, in mass percent:
Cu：0.1-1.0%，S：0.005-0.010%。
3. the hot-dip plated high strength steel sheet according to claim 1, wherein the austenite volume fraction of the base plate is 20% or less at 800 ℃.
4. A method for producing a hot dip plated high strength steel sheet according to any one of claims 1 to 3, comprising the steps of:
obtaining a substrate slab with the chemical composition identical to that of the substrate;
heating, rough rolling, finish rolling, cooling, coiling, cold rolling and continuous annealing are carried out on the substrate plate blank to obtain an annealed substrate;
carrying out hot galvanizing, heat treatment and finishing on the annealed substrate to obtain the hot dip high-strength steel plate;
wherein:
the chemical components of the hot galvanizing plating solution are the same as those of the plating layer;
the dew point temperature of the continuous annealing is-40 ℃ to-20 ℃, and the temperature of the annealing substrate is 400-450 ℃ when the hot galvanizing is carried out.
5. The method for producing a hot-dip plated high strength steel sheet according to claim 4, wherein the end temperature of the heating is 1100 to 1200 ℃.
6. The method for producing a hot-dip plated high strength steel sheet according to claim 4, wherein the temperature of the heat treatment is 450-550 ℃ and the time of the heat treatment is 10-20s.
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