CN111148855B - Method for producing a steel sheet, steel sheet and use thereof - Google Patents
Method for producing a steel sheet, steel sheet and use thereof Download PDFInfo
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- CN111148855B CN111148855B CN201880012441.XA CN201880012441A CN111148855B CN 111148855 B CN111148855 B CN 111148855B CN 201880012441 A CN201880012441 A CN 201880012441A CN 111148855 B CN111148855 B CN 111148855B
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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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing 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
- C21D8/0205—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
- 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
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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
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- 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
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- C—CHEMISTRY; METALLURGY
- C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
- C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
- C25D3/00—Electroplating: Baths therefor
- C25D3/02—Electroplating: Baths therefor from solutions
- C25D3/56—Electroplating: Baths therefor from solutions of alloys
- C25D3/565—Electroplating: Baths therefor from solutions of alloys containing more than 50% by weight of zinc
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- C—CHEMISTRY; METALLURGY
- C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
- C25D—PROCESSES FOR THE ELECTROLYTIC OR ELECTROPHORETIC PRODUCTION OF COATINGS; ELECTROFORMING; APPARATUS THEREFOR
- C25D5/00—Electroplating characterised by the process; Pretreatment or after-treatment of workpieces
- C25D5/34—Pretreatment of metallic surfaces to be electroplated
- C25D5/36—Pretreatment of metallic surfaces to be electroplated of iron or steel
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Mechanical Engineering (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Physics & Mathematics (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Electrochemistry (AREA)
- Coating With Molten Metal (AREA)
- Electroplating Methods And Accessories (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention relates to a method for producing a steel sheet, in particular a skin plate for a vehicle, wherein a steel alloy having a desired composition is melted, cast and then rolled to form the steel sheet, wherein the steel alloy is interstitial free steel (IF steel), and wherein the steel sheet is annealed and finished after rolling and is then provided with a metal corrosion protection layer by means of an electrolytic method or evaporation. In order to achieve a low Wsa value with the narrowest spread, niobium in an amount of > 0.01% by weight, preferably > 0.011% by weight, is alloyed to the steel.
Description
The present invention relates to a method for producing a steel sheet having improved visual quality after forming.
In order to further improve the visual appearance of painted automobiles, it has been found that while it is really important to adjust the belt stiffness profile to improve the paint appearance, it is not sufficient. In the production of shaped and coated panels, a number of parameters are important for good visual appearance of the coating.
A basic indicator of good coatability and good paint appearance is a so-called wave surface arithmetric value (Wsa). An article published in 2013, 10, 17 at www.blechnet.com, on board "Neuartige Blechverzinkung bringt Automobillack auf Hochglanz" indicates that a board with a Wsa value of less than 0.35 μm ensures a good paint appearance. First, the article states that low Wsa values are an indicator of good paint appearance. The article continues to write that since the value of Wsa is simultaneously related to the average roughness (Ra), this also affects the formability. According to this article, experience has shown that it is important to reduce the value of Wsa of the sheet material to below 0.35 μm (whereas in conventional sheet materials, Wsa is indeed above 0.5 μm) and at the same time to provide sufficient lubrication pockets for forming, which is successfully achieved by increasing the so-called peak count.
In this case, emphasis is placed on using a leveling roll (skin smoothing roll) to anticipate the subsequent topography of the sheet as a negative margin in a manner similar to that used in printing techniques. To achieve the above-mentioned Wsa value, a new roll texture is produced and the heat treatment in the furnace is also improved.
The Thissenkurp Steel Europe has disclosed a similar report at www.besserlackieren.de, which also includes a description of how the surface finish of the galvanized sheet can be made to a comparable quality.
For example, EP 0234698B 1 discloses a method in which a surface roughness with defined raised areas is produced.
In addition to hot dip galvanization, electrolytic galvanization may be used, or a cathode zinc-based anticorrosive layer may also be applied to a steel sheet using vapor deposition (PVD, CVD, … …). Whereas for hot dip galvanising the strip is just conveyed through a bath of liquid zinc (about 450 ℃), galvanising or application of zinc by means of vapour deposition is carried out at lower temperatures (below 100 ℃ and 300 ℃ respectively).
The surfaces of electrolytically or vapor deposited zinc coatings are significantly different if they are compared to surfaces produced with hot dip galvanization; in particular, electrolytic zinc plating has a high degree of smoothness, but this can be identified as micro-roughness with super-magnification.
Basically, the production of galvanized steel sheets is carried out in such a way that the steel is produced from pig iron in a converter furnace and cast in a continuous casting plant, then rolled in a hot strip mill and then cold rolled. The application of zinc using an electrolytic galvanising process or by means of vapour deposition, annealing and possibly trimming (addressing) before the application of the zinc layer, followed by electrolytic galvanising or by means of vapour deposition, it being possible to apply further layers, such as phosphating, after the application of the zinc.
Austria standard EN10152 discloses continuous electrolytic galvanized parts made of low-alloy steel for cold forming.
The steels mentioned therein are all low alloy steels.
In the automotive field, in particular, IF and BH steels are used for body shells.
IF steel is considered to be "interstitial-free" steel, not containing any interstitial-embedded foreign atoms (small amounts of carbon and nitrogen are completely segregated into carbides and nitrides by means of titanium and/or niobium), and thus has excellent plastic deformability. Such steels are used for deep-drawn parts in automotive engineering.
Bake-hardened steel (BH steel) as part of the baking finish (typically at 170 ℃ for 20min), has a significant increase in yield strength and very good deformability. These steels also have good dent resistance, which is why these steels are often used in body shell applications.
The object of the invention is to provide a method for producing a steel sheet made from IF in the uncoated state or after additional electrolytic coating or also after applying a coating by means of a CVD or DVD process, these steps being carried out with a metal coating such as Zn, ZnNi, ZnCr or another metal coating acting as an anti-corrosion coating, whereby the desired Wsa values in the deformed state can be better achieved and the range reliably maintained.
This object is achieved by means of a method having the features of claim 1.
Advantageous modifications are disclosed in the dependent claims.
Measurements of the Wsa values were made on macintoke (Marciniak) tensile test pieces using SEP1941 at 5% deformation, but in the rolling direction.
According to the present invention, it has been determined that it is impossible to reliably and absolutely maintain the Wsa value of the vehicle body shell member in the deformed state within the desired range of < 0.35 μm only by optimizing the degree of long waving in the non-deformed state.
According to the invention, it has been determined that by carrying out the selective step on the material, the longwaviness limit required in the deformed state is absolutely satisfied.
In other words, particularly by changing the alloy composition in the IF steel used, it is possible to achieve more reliable production of a vehicle body skin material having reduced long waviness in a deformed state.
Accordingly, it has been determined according to the invention that a guaranteed adjustment of the long corrugation, which is reduced in the deformed state, can be achieved by adding niobium to the alloy in a percentage by weight of > -0.02%, in particular in IF steels. In particular, for example, the Wsa values of steel types DC04 to DC07 can be stabilized at a level below 0.30 μm.
When IF steel is used, the Wsa level can be stabilized to an average of 0.29 μm IF the general titanium concept is not used for the body cover sheet material but the titanium-niobium concept is used.
The results also show that advantageously, after addition of Nb to the steel, the heating rate of the recrystallization annealing can be varied over a wide range without negatively affecting the Wsa value. According to the invention, these heating rates are from 5 to 30K/s.
After recrystallization annealing, a trim or temper rolling process is used to adjust the mechanical properties and selectively affect the surface roughness. In the course of this procedure, both the roughness and the long waviness are transmitted from the rolls to the strip.
The invention will be illustrated by way of example on the basis of several figures. In the drawings:
FIG. 1: shows a comparison of the longwaviness in the IF steel conditioned in the uncoated state according to the prior art (to example 48) with the modified Wsa value according to the invention before and after deformation (starting from example 49);
FIG. 2: shows the relationship between the niobium content in the base material (IF steel after trimming) in the deformed state and the measured Wsa value; is not coated;
FIG. 3: showing a comparison of the degree of long corrugation in the IF steel after deformation in the uncoated state and after trimming in the electrolytically galvanized state;
FIG. 4: the alloys according to the invention are shown in tabular form;
FIG. 5: a table showing preferred alloy ranges;
FIG. 6: a table showing particularly preferred alloy ranges;
FIG. 7: a table illustrating several exemplary embodiments; according to the invention and comparative examples.
Figure 1 shows a conventional IF steel (to example 48) produced and processed according to the prior art. A considerable enlargement (expansion) of the Wsa value during deformation is evident. Starting from example 49, which is an IF steel according to the invention, the Wsa value is significantly improved and the enlargement is significantly reduced. It is clear that with the present invention this value can be reliably maintained at about 0.30 μm or below 0.30 μm. In this case, the light bars represent the value of Wsa in the non-deformed state, and the black bars represent the values in the deformed state.
FIG. 2: clearly shows the relationship between the niobium content in the substrate (IF steel) and the measured Wsa value in the trimmed uncoated steel in deformed state. Not only does the Wsa value decrease, but the expansion also decreases significantly as the Nb content increases.
According to the invention, a niobium content of > 0.02% by weight (200 ppm) is set in the alloy. According to the present invention, the niobium content is preferably set to 0.021 to 0.15% by weight, more preferably 0.021 to 0.10% by weight, and even more preferably 0.021 to 0.05% by weight. With these values, it is possible to achieve very good values of Wsa.
Fig. 3 shows that the change in the value of Wsa is hardly affected by the galvanizing process.
By using suitable skin smoothing rolls, the waviness value of the metal-coated strip in the undeformed state can be reduced to a low level. However, in the deformed state, this improvement no longer exists.
The degree of trimming is between 0.5 and 0.75%.
By adding Nb, little or no increase in the value of Wsa due to deformation can be achieved.
The IF steel produced according to the invention shows, in particular after deformation, significantly better properties than conventional IF steels according to the prior art.
According to the invention, the IF steel may have an alloy composition according to fig. 4 (all values are percentages by weight);
preferably, the IF steel has a composition according to fig. 5;
a particularly preferred range for IF steels is shown in fig. 6;
the remainder consists of iron and impurities resulting from the smelting, respectively.
Fig. 2 shows the corresponding measured relationship in IF steel, showing the post-deformation Wsa value plotted against the niobium content. In this case, it is apparent that the Wsa value steadily improved as the Nb content increased. It is presumed that this relationship also exists when more than 0.03% by weight of niobium is added to the alloy. However, according to the scope of the present invention, on the one hand a sufficient reduction of the value of Wsa is allowed and on the other hand an undesired hardening effect in the substrate is prevented, which would lead to a reduction of the deformability.
The roll roughness (Ra) of the dressing step is set to a value between 1.6 and 3.3 μm for low and long waviness in the non-deformed state and in the subsequent deformed state, so that the roughness value in the strip can be maintained as desired by the customer. The Wsa value can be further reduced by reducing the roll roughness value, but this requires a reduction in the customer's roughness specification.
All conventional metallic coating materials according to the prior art can be used as coating materials in the electrolytic deposition process. This includes in particular but not exclusively zinc alloys.
In the present invention, advantageously, by taking the steps of alloying in the steel, the Wsa value can be successfully set to a very low level in a very stable manner.
The following examples should illustrate that the niobium content has a positive effect on the formation of the level of the Wsa value in the shaped part (measured in a macinton test piece with 5% deformation) and should be distinguished from other effects.
In the examples of coating variants Z listed below, the strip speed and the deposition conditions are also indicated for the sake of completeness. They are within the parameters customary according to the prior art, but have no significant effect on the value of Wsa in the deformed state.
FIG. 1: examples of the value of Wsa measured in the IF steels according to the prior art (to example 48) and according to the invention (starting from example 49).
The results show that it is advantageous to comply with the following conditions:
N*(Ti+Nb)*S*10^6
provided that
With pure zinc coating (Z), the product is equal to or greater than 1, and with zinc magnesium coating (ZM), the product is equal to or greater than 2.
According to the present invention, it is therefore possible to ensure that a rougher deposit is formed. This results in better deformability without negatively affecting strength.
FIG. 2: the relationship between the Nb content in the steel after deformation and the Wsa value is shown.
FIG. 3: the Wsa values for uncoated steel and after electrolytic galvanization are shown.
Claims (20)
1. A method of producing a steel sheet, wherein a steel alloy having a desired composition, which is a steel alloy in the form of a slab, is smelted, poured, and then rolled into a sheet
A) Interstitial free steel (IF steel)
And after rolling, the steel plate is rolled
B) Annealing and finishing the mixture to obtain the finished product,
characterized in that niobium is added to the steel alloy in an amount of > 0.01% by weight in order to achieve a low Wsa value with the narrowest possible enlargement, wherein the alloy satisfies the following condition: n (Ti + Nb) S10 ^6, the product is greater than 1, and the heating rate of annealing is between 5K/S and 30K/S.
2. Method according to claim 1, characterized in that niobium is added to the steel alloy in a content > 0.011% by weight.
3. Method according to claim 1, characterized in that niobium is added to the steel alloy in an amount of > 0.02% by weight.
4. The method according to claim 1, wherein the alloy satisfies the following condition: n (Ti + Nb) S10 ^6, and the product is more than 1.5.
5. The method according to claim 1, characterized in that IF steel is smelted,% by weight having the following analysis:
the remainder consists of iron and impurities resulting from the refining.
6. The method according to claim 1, characterized in that IF steel is smelted,% by weight having the following analysis:
the remainder consists of iron and impurities resulting from the refining.
7. The method according to claim 1, characterized in that IF steel is smelted,% by weight having the following analysis:
the remainder consists of iron and impurities resulting from the refining.
8. Method according to any of claims 5-7, wherein the IF steel further comprises one or more of the following elements:
up to 100ppm of boron and/or
Up to 0.4% by weight vanadium and/or
Up to 0.4% by weight of zirconium
The remainder consists of iron and impurities resulting from the refining.
9. The method according to claim 1, characterized in that IF steel is smelted,% by weight having the following analysis:
the remainder consists of iron and impurities resulting from the refining.
10. The method according to claim 1, characterized in that IF steel is smelted,% by weight having the following analysis:
the remainder consists of iron and impurities resulting from the refining.
11. The method according to claim 1, characterized in that IF steel is smelted,% by weight having the following analysis:
the remainder consists of iron and impurities resulting from the refining.
12. Method according to any of claims 9-11, wherein the IF steel further comprises one or more of the following elements:
up to 100ppm of boron, and/or
Up to 0.4% by weight of vanadium, and/or
Up to 0.4% by weight of zirconium, and/or
Up to 0.5% by weight hafnium, and/or
Up to 0.5% by weight of tungsten, and/or
Up to 0.5% by weight tantalum, and/or
The remainder consists of iron and impurities resulting from the refining.
13. A method according to claim 1, characterized in that after the finishing, the steel sheet is provided with a metal anti-corrosion coating by means of an electrolytic process or by means of vapour deposition.
14. Method according to claim 13, characterized in that the metal anti-corrosion coating is applied electrolytically or by means of CVD and PVD processes, the metal coating consisting of or being based on zinc.
15. The method of claim 14, wherein the metal coating is a zinc-chromium coating, zinc-nickel, zinc-magnesium, zinc-titanium, zinc-calcium, or a zinc alloy with zirconium, hafnium, cerium.
16. The method according to claim 1, characterized in that a smoothing roll having a roughness (Ra) of 1.6 to 3.3 μ ι η is used.
17. The method of claim 1, wherein the degree of trimming is between 0.5 and 0.75%.
18. The method of claim 1, wherein the steel sheet is a body skin panel of a vehicle.
19. Steel sheet produced according to the method of any one of the preceding claims having a composition according to any one of claims 5-12.
20. Use of the steel sheet according to claim 19 for body shell parts and buildings for motor vehicles.
Applications Claiming Priority (5)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| DE102017103303.3A DE102017103303A1 (en) | 2017-02-17 | 2017-02-17 | Method for producing steel sheets |
| DE102017103303.3 | 2017-02-17 | ||
| DE102017103299.1 | 2017-02-17 | ||
| DE102017103299 | 2017-02-17 | ||
| PCT/EP2018/053885 WO2018149967A1 (en) | 2017-02-17 | 2018-02-16 | Method for producing steel sheets, steel sheet and use thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN111148855A CN111148855A (en) | 2020-05-12 |
| CN111148855B true CN111148855B (en) | 2021-10-01 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201880012441.XA Active CN111148855B (en) | 2017-02-17 | 2018-02-16 | Method for producing a steel sheet, steel sheet and use thereof |
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| Country | Link |
|---|---|
| KR (1) | KR102321290B1 (en) |
| CN (1) | CN111148855B (en) |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103774043A (en) * | 2013-12-31 | 2014-05-07 | 首钢总公司 | Hot-galvanized steel plate for automobile side wall outer panel and production method thereof |
| CN104204309A (en) * | 2012-04-13 | 2014-12-10 | 新日铁住金株式会社 | Electroplating steel sheet, electroplated steel sheet, and manufacturing method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06256901A (en) * | 1993-03-04 | 1994-09-13 | Sumitomo Metal Ind Ltd | High tensile strength cold rolled steel sheet for deep drawing and its production |
| KR100797238B1 (en) * | 2006-12-26 | 2008-01-23 | 주식회사 포스코 | The method for manufacturing thin steel sheet for deep drawing having excellent workability |
| BR112015007044B1 (en) * | 2012-10-03 | 2020-11-10 | Nippon Steel Corporation | galvanized steel sheet with annealing and method to produce the same |
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2018
- 2018-02-16 KR KR1020197024965A patent/KR102321290B1/en active IP Right Grant
- 2018-02-16 CN CN201880012441.XA patent/CN111148855B/en active Active
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104204309A (en) * | 2012-04-13 | 2014-12-10 | 新日铁住金株式会社 | Electroplating steel sheet, electroplated steel sheet, and manufacturing method thereof |
| CN103774043A (en) * | 2013-12-31 | 2014-05-07 | 首钢总公司 | Hot-galvanized steel plate for automobile side wall outer panel and production method thereof |
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| Publication number | Publication date |
|---|---|
| CN111148855A (en) | 2020-05-12 |
| KR20190112298A (en) | 2019-10-04 |
| KR102321290B1 (en) | 2021-11-05 |
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