WO2005083140A1 - 高強度極薄冷延鋼板、その製造方法、それを用いたガスケット用材料およびそれを用いたガスケット材 - Google Patents
高強度極薄冷延鋼板、その製造方法、それを用いたガスケット用材料およびそれを用いたガスケット材 Download PDFInfo
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- WO2005083140A1 WO2005083140A1 PCT/JP2005/002931 JP2005002931W WO2005083140A1 WO 2005083140 A1 WO2005083140 A1 WO 2005083140A1 JP 2005002931 W JP2005002931 W JP 2005002931W WO 2005083140 A1 WO2005083140 A1 WO 2005083140A1
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Classifications
-
- 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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
Definitions
- the present invention relates to a high-strength ultra-thin cold-rolled steel sheet having excellent workability and spring properties, which is used as a sealing material for each opening including a cylinder in an internal combustion engine, a method for producing the same, and a method for producing the same.
- the present invention relates to a gasket material used and a gasket material using the same. In particular, it relates to materials represented by gaskets for sealing automobile engines.
- the asbestos substitute material a material obtained by performing composite processing with a mild steel sheet using aramide fiber or graphite is used. As a completely different structure from the conventional gasket, a stainless steel coated with rubber paint is also used.
- Patent Document 1 Japanese Patent Application Laid-Open No. 09-194935
- Patent Document 2 JP-A-2000-109957
- FIG. 3 is a schematic cross-sectional view showing a usage mode of the gasket material.
- a bead portion 42 is formed in the gasket material 41 interposed between the cylinder 43 and the cylinder head 44 in order to improve the sealing performance.
- the requirements for the gasket material 41 are the workability and the spring property at the time of bead processing. This workability and springiness are contradicting metallurgy.
- a high-strength ultrathin cold-rolled material which is inexpensive, has excellent gas sealing properties and is excellent in spring properties while harmonizing good workability with spring properties.
- An object of the present invention is to provide a steel sheet and a method for manufacturing the same.
- Still another object of the present invention is to provide a cylinder opening having a particularly good resiliency required for sealing performance, and various openings such as a cooling water opening, a lubricating oil opening, and a bolt hole.
- the purpose of the present invention is to provide a gasket material having excellent spring properties, which can be well adapted to various types of materials and has good sealing properties with a good spring property.
- S. ”) requires 800MPa or more.
- the gasket must have an elongation of 8% or more (total elongation: hereinafter referred to as “T. EL.”) For bead processing.
- the strength f and the tensile strength (T.S.) of IS5 piece need to be 700MPa or more.
- the steel constituting the high-strength ultra-thin cold rolled steel sheet is one or two of the following: Ti: 0.01-0.2%, Nb: 0.05-0.1%, and B: 0.001-0.01%.
- the cold-rolled steel sheet preferably contains ferrite having an average grain size of 5 zm to 12 ⁇ m and martensite having an average grain size of 5 ⁇ m or less, and has a volume fraction of 30%. It is desirable to have the following martensite structure.
- the method for producing a high-strength ultrathin cold-rolled steel sheet according to claim 4 is, by weight%, C: 0.03-0.20%, Si: ⁇ 0.5%, Mn: 0.5-3.0%, P: ⁇ 0.1%, S: ⁇ 0.06%, A1: ⁇ 0.1%, N: 0.0010-0.0160%, hot-worked continuous structure consisting of Fe and unavoidable impurities so that the average grain size is 5 ⁇ or less. Rolling, pickling and then cold rolling at a rolling rate of 30-90%.
- the method for producing a high-strength ultra-thin cold-rolled steel sheet according to claim 5 is, by weight%, C: 0.03-0.20%, Si: ⁇ 0.5%, Mn: 0.5-3.0%, P: ⁇ 0.1%, S: ⁇ 0.06%, A1: ⁇ 0.1%, N: 0.0010-0.0160%, hot-worked continuous structure consisting of Fe and unavoidable impurities so that the average grain size is 5 ⁇ or less.
- Rolling, pickling, cold rolling at a rolling rate of 30 to 90%, continuous annealing at 700 ° C or more or box annealing at 550 ° C or more, and secondary rolling at a rolling rate of 60% or less Rolling or temper rolling is performed.
- the method for producing a high-strength ultrathin cold-rolled steel sheet according to claim 6 is, by weight%, C: 0.03-0.20%, Si: ⁇ 0.5%, Mn: 0.5-3.0%, P: ⁇ 0.1%, S: ⁇ 0.06%, A1: ⁇ 0.1%, N: 0.0010-0.0160%, heat the continuous structure consisting of Fe and unavoidable impurities so that the average crystal grain size is 5 xm or less.
- the gasket material according to claim 8 is, by weight%, C: 0.03-0.20%, Si: ⁇ 0.5%, Mn: 0.5-3.0%, P: ⁇ 0.1%, S: ⁇ 0.06%, Al: ⁇ 0.1%, N: 0.0010 0.0160%, the continuous structure consisting of Fe and unavoidable impurities, average grain size Hot rolled so as to be 5 ⁇ m or less, pickling, cold rolling at a rolling rate of 30-90%, and zinc or nickel plating on the surface.
- the gasket material according to claim 9 is, by weight%, C: 0. 03-0.20%, Si: ⁇ 0.5%, Mn: 0.5-3.0%, P: ⁇ 0.1%, S: ⁇ 0.06%, Al: ⁇ 0.1%, N: 0.0010 0.0160%, the continuous structure consisting of Fe and unavoidable impurities, average grain size Hot rolling to a force of ⁇ ⁇ or less, after pickling, cold rolling at a rolling rate of 30-90%, and then continuous annealing at 700 ° C or more or box-type annealing at 550 ° C or more It is characterized by being subjected to secondary rolling or temper rolling at a rolling ratio of 60% or less, and then to Zn or Ni plating on the surface.
- the gasket material according to claim 10 is, in terms of% by weight, C: 0. 03-0.20%, Si: ⁇ 0.5%, Mn: 0.5-3.0%, P: ⁇ 0.1%, S: ⁇ 0.06%, Al: ⁇ 0.1%, N: 0.0010—0.0160%, the continuous grain consisting of balance Fe and unavoidable impurities, average grain Hot-rolled so that the diameter is 5 ⁇ or less, after pickling, cold-rolled at a rolling rate of 30 to 90%, and then annealed by continuous annealing or box-type annealing, and then a rolling rate of 60% or less Secondary rolling, followed by continuous annealing at 700 ° C or higher or box-type annealing at 550 ° C or higher, followed by tertiary rolling or temper rolling at a rolling reduction of 60% or less, and further Zn coating on the surface.
- the gasket material according to any one of claims 8 to 10 is, in terms of steel weight% by weight constituting the gasket material, Ti: 0.01-0.2%, Nb: 0.005-0.1. . /. And B: 0.001 0.01. /. Of these, it is desirable to further contain one or two of them.
- the gasket material according to claim 12 is the gasket material according to any one of claims 8 to 11. It is characterized by being manufactured using a gasket material.
- FIG. 1 is a schematic diagram of a method for evaluating the workability of a gasket.
- FIG. 2 is a schematic diagram of a test method for evaluating spring properties.
- FIG. 3 is a schematic cross-sectional view showing a usage mode of a gasket material for a spring.
- FIG. 4 is a schematic cross-sectional view showing a usage mode of a gasket material having a bent estuary.
- T indicates the compression amount
- T1 indicates the restoration amount
- 41 indicates the gasket material
- 42 indicates the bead portion.
- the steel components of the high-strength ultra-thin cold-rolled steel sheet used as the material for the gasket as the base sheet of the present invention are, by weight%, C: 0.03-0.20%, Si: ⁇ 0.5%, Mn : 0.5-3.0%, P: ⁇ 0.1%, S: ⁇ 0.06%, Al: ⁇ 0.1%, N: 0.0010-0.160%, balance Fe and inevitable It consists of various impurities. Ti: 0.01-0.2%, Nb: 0.005-0.1%, and B: 0.001 0.0
- C is desirably at least 0.03% by weight because of the high degree of tempering of a high-strength ultrathin cold-rolled steel sheet used as a gasket material.
- C exceeds 0.2% by weight, the amount of carbide precipitation increases and the workability of the steel sheet decreases, and at the same time, the load of cold rolling increases, the shape deteriorates, and the steel sheet passes through the continuous annealing process. It may cause a decrease in productivity such as inhibition of sex. Therefore, in the present invention, the upper limit of the component C is set to 0.20% by weight.
- Si has a large solid solution strengthening function in steel and is an effective element for obtaining spring properties. Therefore, 0.1% by weight or more is necessary. Also, Si is better in terms of material strengthening, the more, the better, but the load of cold rolling increases and the shape is deteriorated, so the upper limit is set to 0.50% by weight.
- Mn is a component necessary for preventing red hot embrittlement during hot rolling due to S, which is an impurity, and at the same time, imparts a high degree of tempering to the original sheet as in the case of C, so that the Mn component is 0. 5% by weight or more.
- the upper limit of Mn component is set to 3.0% by weight.
- P is a component for refining crystal grains, and increases the strength of the original plate, so that it adds a certain amount of calorie and impairs corrosion resistance.
- the corrosion resistance, particularly the pitting resistance is remarkably reduced. Therefore, the upper limit of the P component is set to 0.10% by weight.
- S is an impurity component that causes red-hot embrittlement during hot rolling, and is desirably as small as possible. However, it cannot completely prevent contamination from iron ore and the like, and desulfurization during the process is difficult. Therefore, some residuals are unavoidable. Since the red embrittlement due to a small amount of residual S can be reduced by Mn, the upper limit of the S component is set to 0.06% by weight.
- A1 is added to the steel bath as a deoxidizing agent during steelmaking.
- A1 is used as an oxidation inhibitor during continuous production and as an anti-seizure agent for molds during continuous production.
- the excess A1 reacts with the oxygen in the type I powder used, inhibiting the original powder effect. Therefore, the amount of A1 should be 0.10% by weight or less.
- N gives a high degree of tempering to the original plate, similar to C and Mn. Although it is a necessary component for strengthening the steel, if it is less than 0.001% by weight, it will cause difficulty in steel making. The stability of the product is remarkably reduced due to a decrease in the yield, and the anisotropy during press molding is significantly deteriorated. Further, cracks occur on the surface of the continuous structure, which causes structure defects. Therefore, in the present invention, the range of the N component is set to 0.001 to 0.01% by weight.
- Ti and Nb form a carbonitride compound and have an effect of immediately refining crystal grains.
- the lower limit of Nb is 0.005% by weight, and 1 is 0.01% by weight.
- the recrystallization temperature must be raised and the continuous annealing temperature must be raised, which increases costs. Therefore, the upper limit of Ti is set to 0.2% by weight, and the upper limit of Nb is set to 0.1% by weight.
- B is an element necessary for obtaining martensite, which is an important structure of the present invention, and has the effect of reducing segregation and grain coarsening in the grain boundary to refine the crystal grains. If necessary, add 0.001% by weight or more. Also, since the effect is saturated even if it is too much, the upper limit of the B component is set to 0.01% by weight for reasons such as cost.
- N is preferably 1100 ° C or more from the viewpoint of active decomposition and solid solution of N and stable securing of hot finish rolling temperature. If the hot rolling finish temperature is lower than the Ar3 point, the crystal structure of the hot steel strip is mixed and coarsened, and the desired strength cannot be obtained.Therefore, the hot rolling finish temperature should be higher than the Ar3 point. desirable.
- the rolling ratio and cooling conditions in the hot rolling finish rolling are not specified, but in order to obtain high strength, it is desirable to perform rapid cooling under as high pressure as possible so that the average crystal grain size is 5 zm or less. Further, it is desirable that the structure has a structure in which martensite is dispersed in ferrite having an average particle size of 5 x m or less.
- the winding temperature is not specified in the present invention, the winding temperature is desirably 700 ° C. or less in order to suppress the coarsening of the crystal grains.
- the steel sheet hot-rolled with the above-mentioned component system is cold-rolled.
- This cold-rolling ratio is an important strength factor of the present invention together with the components, and in order to obtain a desired strength, 30-90% Do with.
- the material that has been cold-rolled at a rolling rate of 30 to 90% as described above is degreased in the cleaning process and then annealed at a temperature of 700 ° C or higher for continuous annealing or 550 ° C or higher for batch annealing. I do.
- the upper limit temperature is 830 ° C for continuous annealing and 700 ° C for box type annealing.
- the strength of the secondary cold rolling after annealing increases as the rolling reduction increases, and is desirable. However, the elongation decreases. Therefore, when performing secondary cold rolling, the rolling reduction should be 60% or less. Thereafter, if necessary, surface roughness is imparted by temper rolling.
- the cold-rolled steel sheet produced as above consists of ferrite with an average grain size of 5 xm to 12 zm or less and martensite with an average grain size of 5 ⁇ m or less and a volume fraction of 30% or less. It is desirable to have an organization. For spring applications, it is more desirable to have a structure in which ferrite having an average particle size of 2 zm or less and martensite having an average particle size of 5 ⁇ m or less have a volume fraction of 6% 30% or less. In processing applications, microstructures consisting of ferrite with an average particle size of —12 zm and martensite with an average particle size of 5 ⁇ m or less by volume percentage of 5% or less.
- a cold-rolled steel sheet with an important spring property can have a finer structure and higher workability.
- examples of the steel sheet of the present invention prepared as described above include a sheet-shaped and coil-shaped steel sheet, a steel foil, and a sheet obtained by performing a surface treatment on the steel sheet.
- electrolytic chromic acid-treated steel sheets or ultra-thin tin-plated steel sheets, nickel-plated steel sheets, zinc-plated steel sheets, and these plated steel sheets have a two-layer structure of metal chromium in the lower layer and chromium hydrated oxide in the upper layer.
- a chromium hydrated oxide or a surface treated with a two-layer structure consisting of a chromium hydrated oxide as the upper layer and a metal chromium layer as the lower layer is superior in terms of corrosion resistance.
- Tables 1 (1/2) and (2/2) show the production conditions such as the steel composition and the rolling reduction, and Table 2 shows the characteristic evaluation results of the examples and comparative examples of the present invention.
- Sample Nos. 1-7 which are examples of the present invention, have high tensile strength and excellent bendability.
- Table 2 shows that for sample Nos. 1-3, which are used for processing purposes, the column for spring properties is X and cannot be applied for spring applications, but the column for bending workability is marked with ⁇ , indicating good bending properties. Yes.
- the mark “ ⁇ ” indicates a good force. The bending force cannot be applied with X.
- Sample No. 814 which is a comparative example, did not satisfy the characteristics of springability and bead workability, and could not be used for spring and katunje applications.
- the X-mark is also shown in the item of the deviation and the deviation).
- FIG. 2 shows the steps of a compression test, which is a test method for evaluating spring properties.
- Fig. 2 (a) shows the state before compression of the machined bead
- Fig. 2 (b) shows the state where a compression load is applied
- Fig. 2 (c) shows the state where the compression load is removed. Show.
- a compression load was applied to the bead portion from above using a compression tester. After the load was unloaded, a sample whose restoring amount (T1) exceeded 40% with respect to the compressing amount (T) was indicated by ⁇ because the spring property passed. On the other hand, when the restoration amount (T1) was 40% or less, the panel property was X and the specimen was rejected.
- the bendability was evaluated by subjecting the sample to 180 ° bending at 0T and checking for the occurrence of cracking force in the sample.
- the case where a crack occurred was represented as X, and was rejected.
- the case where no crack was generated was represented by ⁇ , and the test was passed. Samples having an elongation of 15% or more had good bending workability.
- the gasket material of the present invention can be used as a spring application in which workability and springability are balanced or a processing application excellent in 0T bending workability by slightly changing the manufacturing method. Thus, all have excellent gas sealing properties.
- the gasket material further subjected to surface treatment exhibits excellent corrosion resistance even when exposed to a high temperature state, and exhibits stable gas sealing properties for a long period of time.
- the gasket material of the present invention has particularly good spring characteristics required for sealing performance of an opening for a cylinder in a spring application, and has various characteristics such as a cooling water opening, a lubricating oil opening, and a bolt hole.
- the opening can also be suitably used. In processing applications, it cannot be applied to spring applications, but it can be suitably used for various openings such as cooling water openings, lubricating oil openings, and bolt holes.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
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- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Gasket Seals (AREA)
Abstract
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Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
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JP2004053061A JP4785171B2 (ja) | 2004-02-27 | 2004-02-27 | バネ用高強度極薄冷延鋼板の製造方法 |
JP2004-053061 | 2004-02-27 |
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WO2005083140A1 true WO2005083140A1 (ja) | 2005-09-09 |
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JP6056333B2 (ja) * | 2012-09-28 | 2017-01-11 | Jfeスチール株式会社 | 極薄冷延鋼板の製造方法 |
KR101585749B1 (ko) * | 2013-12-26 | 2016-01-14 | 주식회사 포스코 | 라미네이트 강판용 박강판, 이의 제조방법 및 이를 이용한 경량 라미네이트 강판 |
Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
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JPH09194935A (ja) * | 1996-01-10 | 1997-07-29 | Toyo Kohan Co Ltd | ばね性に優れたガスケット材用冷延鋼板の製造法およびガスケット材 |
JP2003247045A (ja) * | 2001-10-03 | 2003-09-05 | Kobe Steel Ltd | 伸びフランジ性に優れた複合組織鋼板およびその製造方法 |
JP2003321727A (ja) * | 2002-05-01 | 2003-11-14 | Kobe Steel Ltd | 曲げ加工性に優れた低降伏比型高張力鋼板およびその製造方法 |
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JPH08325670A (ja) * | 1995-03-29 | 1996-12-10 | Kawasaki Steel Corp | 製缶時の深絞り性及びフランジ加工性と、製缶後の表面性状とに優れ、十分な缶強度を有する製缶用鋼板及びその製造方法 |
JP3473480B2 (ja) * | 1999-03-18 | 2003-12-02 | 住友金属工業株式会社 | 強度と延性に優れる溶融亜鉛めっき鋼板およびその製造方法 |
JP3823613B2 (ja) * | 1999-06-24 | 2006-09-20 | 住友金属工業株式会社 | 高張力溶融亜鉛めっき鋼板の製造方法 |
JP3882472B2 (ja) * | 2000-06-27 | 2007-02-14 | 住友金属工業株式会社 | 耐衝撃性に優れた高張力鋼板と製造方法 |
JP3858146B2 (ja) * | 2002-01-29 | 2006-12-13 | Jfeスチール株式会社 | 高強度冷延鋼板および高強度溶融亜鉛めっき鋼板の製造方法 |
JP4138465B2 (ja) * | 2002-11-29 | 2008-08-27 | 東洋鋼鈑株式会社 | ばね性に優れたガスケット材用冷延鋼板、その製造方法およびばね性に優れたガスケット材 |
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- 2004-02-27 JP JP2004053061A patent/JP4785171B2/ja not_active Expired - Fee Related
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Patent Citations (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH09194935A (ja) * | 1996-01-10 | 1997-07-29 | Toyo Kohan Co Ltd | ばね性に優れたガスケット材用冷延鋼板の製造法およびガスケット材 |
JP2003247045A (ja) * | 2001-10-03 | 2003-09-05 | Kobe Steel Ltd | 伸びフランジ性に優れた複合組織鋼板およびその製造方法 |
JP2003321727A (ja) * | 2002-05-01 | 2003-11-14 | Kobe Steel Ltd | 曲げ加工性に優れた低降伏比型高張力鋼板およびその製造方法 |
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JP4785171B2 (ja) | 2011-10-05 |
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