JPH04346626A - Manufacture of corrosion resistant hot rolled steel sheet high in productive efficiency and excellent in deep drawability - Google Patents
Manufacture of corrosion resistant hot rolled steel sheet high in productive efficiency and excellent in deep drawabilityInfo
- Publication number
- JPH04346626A JPH04346626A JP3116197A JP11619791A JPH04346626A JP H04346626 A JPH04346626 A JP H04346626A JP 3116197 A JP3116197 A JP 3116197A JP 11619791 A JP11619791 A JP 11619791A JP H04346626 A JPH04346626 A JP H04346626A
- Authority
- JP
- Japan
- Prior art keywords
- steel sheet
- hot
- rolling
- rolled steel
- descaling
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Withdrawn
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 89
- 239000010959 steel Substances 0.000 title claims abstract description 89
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 23
- 230000007797 corrosion Effects 0.000 title claims abstract description 20
- 238000005260 corrosion Methods 0.000 title claims abstract description 20
- 238000005096 rolling process Methods 0.000 claims abstract description 53
- 229910052751 metal Inorganic materials 0.000 claims abstract description 39
- 239000002184 metal Substances 0.000 claims abstract description 39
- 239000000843 powder Substances 0.000 claims abstract description 37
- 238000005098 hot rolling Methods 0.000 claims abstract description 26
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 22
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 19
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 14
- 239000000956 alloy Substances 0.000 claims abstract description 14
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 11
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 11
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 9
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims abstract description 9
- 230000009466 transformation Effects 0.000 claims abstract description 5
- 238000007747 plating Methods 0.000 claims description 50
- 239000010410 layer Substances 0.000 claims description 16
- 238000004804 winding Methods 0.000 claims description 15
- 239000011701 zinc Substances 0.000 claims description 15
- 238000002844 melting Methods 0.000 claims description 13
- 230000008018 melting Effects 0.000 claims description 13
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 10
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 8
- 239000002245 particle Substances 0.000 claims description 8
- 230000003746 surface roughness Effects 0.000 claims description 8
- 239000011247 coating layer Substances 0.000 claims description 3
- 238000003618 dip coating Methods 0.000 claims description 3
- 229910052745 lead Inorganic materials 0.000 abstract description 2
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 238000000034 method Methods 0.000 description 29
- 238000010438 heat treatment Methods 0.000 description 12
- 239000000463 material Substances 0.000 description 12
- 238000005461 lubrication Methods 0.000 description 11
- 238000002347 injection Methods 0.000 description 8
- 239000007924 injection Substances 0.000 description 8
- 230000008569 process Effects 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 239000006104 solid solution Substances 0.000 description 6
- 238000006243 chemical reaction Methods 0.000 description 5
- 150000002739 metals Chemical class 0.000 description 5
- 238000001556 precipitation Methods 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 238000002474 experimental method Methods 0.000 description 4
- 238000006722 reduction reaction Methods 0.000 description 4
- 238000005507 spraying Methods 0.000 description 4
- 238000005275 alloying Methods 0.000 description 3
- 230000006866 deterioration Effects 0.000 description 3
- 238000011161 development Methods 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 239000007788 liquid Substances 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 230000009467 reduction Effects 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 229910052717 sulfur Inorganic materials 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 229910001297 Zn alloy Inorganic materials 0.000 description 2
- 238000005422 blasting Methods 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 239000010960 cold rolled steel Substances 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 238000005868 electrolysis reaction Methods 0.000 description 2
- 238000009713 electroplating Methods 0.000 description 2
- 238000007730 finishing process Methods 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000011261 inert gas Substances 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 230000001590 oxidative effect Effects 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 239000007921 spray Substances 0.000 description 2
- 239000002344 surface layer Substances 0.000 description 2
- 238000007751 thermal spraying Methods 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910000611 Zinc aluminium Inorganic materials 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- HXFVOUUOTHJFPX-UHFFFAOYSA-N alumane;zinc Chemical compound [AlH3].[Zn] HXFVOUUOTHJFPX-UHFFFAOYSA-N 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000004069 differentiation Effects 0.000 description 1
- 230000005611 electricity Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 150000002431 hydrogen Chemical class 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 238000009434 installation Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 230000001050 lubricating effect Effects 0.000 description 1
- 239000010687 lubricating oil Substances 0.000 description 1
- 239000006247 magnetic powder Substances 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000010298 pulverizing process Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 239000010731 rolling oil Substances 0.000 description 1
- 150000003839 salts Chemical class 0.000 description 1
- 238000005488 sandblasting Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- -1 zinc Chemical class 0.000 description 1
Landscapes
- Coating By Spraying Or Casting (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【0001】0001
【産業上の利用分野】本発明はZn,Al,Pb等の単
一金属或いはその合金のめっきを生産性良く、かつ経済
的に施す耐蝕性を有するr平均値1.4以上の深絞り用
熱延鋼板の製造方法に関するものである。[Industrial Application Field] The present invention is for deep drawing with corrosion resistance and r average value of 1.4 or more for plating single metals such as Zn, Al, Pb, etc. or their alloys with good productivity and economically. The present invention relates to a method for manufacturing hot rolled steel sheets.
【0002】0002
【従来の技術】従来、熱間圧延鋼板等に亜鉛等の金属を
めっきするには、熱間圧延工程後に一旦冷却後、酸洗し
た酸洗板を亜鉛や合金等の金属の溶融浴に浸漬する溶融
めっき法や、該酸洗板をめっきしようとする金属の塩を
含んだ溶液中に浸漬し直流電解する電気めっき法等が用
いられていた。[Prior Art] Conventionally, in order to plate hot-rolled steel sheets with metals such as zinc, the pickled sheets were cooled once after the hot-rolling process, and then the pickled sheets were immersed in a molten bath of metals such as zinc or alloys. The hot-dip plating method, in which the pickled plate is immersed in a solution containing the salt of the metal to be plated, and the electroplating method, in which DC electrolysis is performed, have been used.
【0003】しかし、これらの方法では、酸洗設備及び
大型のめっき装置が必要となり、多大の設備費と広大な
設置場所が必要となり、また、溶融めっきでは鋼板を加
熱するための燃料費がかかり、電気めっきでは電解を行
うための電気代がかかるので、経済性の改善が望まれて
いた。[0003] However, these methods require pickling equipment and large-scale plating equipment, which requires a large amount of equipment cost and a vast installation space.Furthermore, hot-dip plating requires high fuel costs to heat the steel plate. Since electroplating requires electricity to perform electrolysis, improvements in economic efficiency have been desired.
【0004】これらの欠点を補う金属めっき方法として
、特開昭54−146230号公報において、熱間圧延
工程中或いは精整ライン中を走行する圧延鋼材外表面に
溶融金属を溶射し、鋼材表層面に均一なめっき層を形成
する方法が提案されている。しかし、この方法は熱間圧
延工程中に形成されるスケールの影響を考慮しておらず
、この方法を実施した場合、スケールの上から溶融金属
を溶射することになるためめっき密着性が悪く、製造後
にプレス加工等が行われる薄鋼板の場合、加工後にめっ
きが剥がれて耐蝕性が悪化する。[0004] As a metal plating method that compensates for these drawbacks, Japanese Patent Application Laid-Open No. 146230/1983 discloses a method in which molten metal is sprayed onto the outer surface of a rolled steel material running in a hot rolling process or a finishing line, and the surface layer of the steel material is A method of forming a uniform plating layer has been proposed. However, this method does not take into account the influence of scale formed during the hot rolling process, and when this method is implemented, the plating adhesion is poor because molten metal is sprayed over the scale. In the case of thin steel sheets that are subjected to press working or the like after manufacturing, the plating peels off after processing, resulting in poor corrosion resistance.
【0005】その上これ等の問題を克服するために必要
な溶射金属の種類や溶射する際の鋼板温度、密着性を向
上させるための鋼板表面の適性粗度、溶射を行う熱間圧
延工程中又は精整ライン上での望ましい位置等について
は記載がなく、実用的な密着性を保証するめっき層を得
るための具体的条件について全く開示も示唆もない。Furthermore, in order to overcome these problems, the type of metal to be sprayed, the temperature of the steel plate at the time of spraying, the appropriate roughness of the steel plate surface to improve adhesion, and the temperature during the hot rolling process during the spraying process. Moreover, there is no description of a desirable position on the finishing line, etc., and there is no disclosure or suggestion of specific conditions for obtaining a plating layer that guarantees practical adhesion.
【0006】さらに特開昭61−204332号公報で
は、300〜800℃の温度範囲で、歪速度300S−
1で仕上げ圧延し、その後400℃以下で巻取った後連
続溶融めっきラインで再結晶、めっき処理を行う。この
方法はα域圧延で高歪速度が必要なため、現状の連続熱
延ラインとしては非常に圧延負荷が大きい。Furthermore, in Japanese Patent Application Laid-Open No. 61-204332, a strain rate of 300 S-
After finishing rolling in step 1 and then winding up at 400°C or lower, recrystallization and plating are performed on a continuous hot-dip plating line. This method requires α-region rolling and a high strain rate, so the rolling load is extremely high for current continuous hot rolling lines.
【0007】一方、熱延鋼板の絞り性を向上させる鋼板
としては、温間圧延で潤滑を施す高r平均値熱延鋼板の
製造方法がある(特開昭61−3844号公報等)。こ
れは、通常の熱延工程を利用してr平均値を向上させる
方法が使用されている。この方法は析出物の固定を目的
に低温加熱を行い、その後α域で高潤滑圧延を行った後
に自己焼鈍もしくは再結晶処理によって高r平均値熱延
鋼板を得るものであった。この方法では、熱延で高濃度
の潤滑を施さなければ十分摩擦係数を下げることができ
ないため、圧延中のスリップを起こす等の障害を伴って
いた。On the other hand, as a method for improving the drawability of a hot-rolled steel sheet, there is a method for producing a hot-rolled steel sheet with a high r average value in which lubrication is applied during warm rolling (Japanese Patent Application Laid-open No. 3844/1984, etc.). This method uses a normal hot rolling process to improve the r average value. In this method, low-temperature heating is performed for the purpose of fixing precipitates, followed by highly lubricated rolling in the α region, followed by self-annealing or recrystallization treatment to obtain a hot-rolled steel sheet with a high r average value. In this method, the coefficient of friction cannot be sufficiently lowered unless high-concentration lubrication is applied during hot rolling, resulting in problems such as slippage during rolling.
【0008】[0008]
【発明が解決しようとする課題】上記に示した温間潤滑
圧延法では、連続的に鋼板を製造している精整ラインで
実施する場合、次記する多大の問題点が生じている。
■低温加熱の実施:通常の熱延工程の加熱温度は、通常
のホットファイナル材が仕上げ温度をAr3以上確保す
るために1100℃以上を確保している。このため温間
潤滑圧延法のように加熱炉を低温にして鋼板を製造する
と、通常加熱温度と低温加熱温度の設定温度変更に要す
る時間のロスが生じ、生産効率を悪化させる。Problems to be Solved by the Invention The above-mentioned warm lubrication rolling method, when carried out on a finishing line that continuously manufactures steel plates, causes the following numerous problems. ■Implementation of low-temperature heating: The heating temperature in the normal hot rolling process is kept at 1100°C or higher in order to ensure the finishing temperature of the normal hot final material to be Ar3 or higher. For this reason, when a steel plate is manufactured using a heating furnace at a low temperature as in the warm lubrication rolling method, there is a loss of time required to change the set temperature between the normal heating temperature and the low temperature heating temperature, which deteriorates production efficiency.
【0009】■α域圧延:仕上げ温度を低温にするため
、粗圧延から、仕上げ圧延までの間で時間調整が必要と
なり、ここでも時間のロスが生じ、同様に生産効率を悪
化させる。
■高潤滑:高潤滑の圧延油を用いるために、通常の製品
を製造する場合は濃度を薄く変える必要があり、さらに
ロールに付着した油を取り除く等の手間が必要となり、
作業性、生産効率を悪化させる。[0009] α-region rolling: In order to lower the finishing temperature, it is necessary to adjust the time between rough rolling and finish rolling, which also causes time loss and similarly deteriorates production efficiency. ■High lubrication: In order to use highly lubricated rolling oil, when manufacturing regular products, it is necessary to change the concentration to a thinner one, and it is also necessary to remove the oil attached to the rolls.
Deteriorates workability and production efficiency.
【0010】■熱延鋼板にZnめっきを施す工程では、
酸による洗浄のため鋼板温度は一旦100℃未満に低下
するため、巻取り後の所要日数を短縮できないばかりか
、コイルの保有熱を利用できず、めっき前の加熱工程で
依然として膨大なエネルギー・長大な加熱炉を必要とす
るため操業コスト低減効果は低い。■In the process of applying Zn plating to hot rolled steel sheets,
Because the temperature of the steel sheet drops below 100℃ due to cleaning with acid, not only is it not possible to shorten the number of days required after winding, but the heat retained in the coil cannot be used, and the heating process before plating still requires a huge amount of energy and time. Since it requires a heating furnace, the effect of reducing operating costs is low.
【0011】本発明は、現状ではエネルギーロスが大き
い高r平均値熱延鋼板に、亜鉛等の単一金属或いはその
合金からなるめっき密着性のよいめっき層を有する耐蝕
性に優れた熱間圧延鋼板を上記の問題を伴わずに、生産
性良く、経済的に製造する方法を提供することを課題と
しており、低コストの商品を提供すると同時にさらに2
つの付加価値、すなわち高r平均値とめっき層による高
耐蝕性を熱延鋼板に付与する技術を提供するものである
。[0011] The present invention provides a hot-rolled steel sheet with excellent corrosion resistance, which has a plating layer with good plating adhesion made of a single metal such as zinc or an alloy thereof, on a hot-rolled steel sheet with a high r average value, which currently has a large energy loss. Our goal is to provide a highly productive and economical method of manufacturing steel plates without the above problems, and at the same time provide low-cost products, we also
The present invention provides a technology for imparting two added values, that is, a high r average value and high corrosion resistance due to a plating layer, to a hot rolled steel sheet.
【0012】0012
【課題を解決するための手段】本発明は、上記課題を達
成するために、重量%で、C:0.05%以下,N:0
.01%以下で、C及びNの含有量と、Ti及びNbの
一方或いは両方の含有量が、0.4(Ti/48+Nb
/93)≦C/12+N/14≦1.2(Ti/48+
Nb/93)の関係にある熱延鋼板用鋼を、、Ar3変
態点以上で熱間圧延を終了した後、700〜800℃で
巻取りを行い、引続き600〜800℃で圧延を行った
後に鋼板を巻取るまでの間に、該鋼板表面のスケールを
ドライデスケーリングまたは高圧水デスケーリングを用
いて除去し、引続き、亜鉛、アルミニウム、鉛等の単一
金属或いはその合金等の金属粉末を前記鋼板の所要の面
に前記金属粉末の融点よりも30℃以上200℃以下の
範囲に高い鋼板温度において噴射して該鋼板の所要の面
に溶融めっき層を形成することを特徴とする耐蝕性熱間
圧延鋼板の製造方法であり、又重量%で、C:0.05
%以下,N:0.01%以下で、C及びNの含有量と、
Ti及びNbの一方或いは両方の含有量が0.4(Ti
/48+Nb/93)≦C/12+N/14≦1.2(
Ti/48+Nb/93)の関係にある熱延鋼板用鋼を
、Ar3変態点以上で熱間圧延を終了した後、700〜
800℃で巻取りを行い、引続き600〜800℃で圧
延を行った後に鋼板を巻取るまでの間に、該鋼板表面の
スケールをドライデスケーリングまたは高圧水デスケー
リングを用いて除去すると共に、表面粗度をRa値で0
.5μm以上とし、引続き亜鉛、アルミニウム、鉛等の
単一金属或いはその合金等の粒度150メッシュ以上の
金属粉末を前記鋼板の所要の面に前記金属粉末の融点よ
りも30℃以上200℃以下の範囲に高い鋼板温度にお
いて噴射して該鋼板の所要の面に溶融めっき層を形成す
ることを特徴とする耐蝕性熱間圧延鋼板の製造方法であ
る。なお、本発明で言う熱延鋼板とは以下に示すC,N
,Nb,Tiの限定を満たし、その他はJIS G3
131の規程を満たすP,S含有量である鋼を示す。[Means for Solving the Problems] In order to achieve the above-mentioned problems, the present invention provides C: 0.05% or less, N: 0% by weight.
.. 01% or less, the content of C and N and the content of one or both of Ti and Nb are 0.4 (Ti/48+Nb
/93)≦C/12+N/14≦1.2(Ti/48+
Nb/93) After hot rolling is completed above the Ar3 transformation point, coiling is performed at 700 to 800°C, and then rolling is performed at 600 to 800°C. Before winding the steel plate, scale on the surface of the steel plate is removed using dry descaling or high-pressure water descaling, and then metal powder such as a single metal such as zinc, aluminum, or lead or an alloy thereof is added to the Corrosion-resistant heat is sprayed onto a required surface of a steel sheet at a steel sheet temperature higher than the melting point of the metal powder in a range of 30° C. or more and 200° C. or less to form a hot-dip coating layer on the required surface of the steel sheet. A method for producing inter-rolled steel sheets, and in weight%, C: 0.05
% or less, N: 0.01% or less, the content of C and N,
The content of one or both of Ti and Nb is 0.4 (Ti
/48+Nb/93)≦C/12+N/14≦1.2(
After hot rolling of a hot-rolled steel plate having a relationship of Ti/48+Nb/93) at Ar3 transformation point or higher,
After winding at 800°C and subsequent rolling at 600 to 800°C, scale on the surface of the steel plate is removed using dry descaling or high-pressure water descaling, and the surface is Roughness is Ra value 0
.. 5 μm or more, and then a metal powder of a single metal such as zinc, aluminum, lead, or an alloy thereof, with a particle size of 150 mesh or more, is applied to the required surface of the steel plate at a temperature of 30°C or more and 200°C or less than the melting point of the metal powder. This is a method for producing a corrosion-resistant hot-rolled steel sheet, characterized in that a hot-dip coating layer is formed on a required surface of the steel sheet by spraying at a high steel sheet temperature. In addition, the hot-rolled steel sheet referred to in the present invention refers to C, N as shown below.
, Nb, Ti, and other JIS G3
Indicates steel with P and S contents that meet the regulations of 131.
【0013】[0013]
【作用】耐蝕性熱延鋼板のr平均値を向上させることは
、鋼板の材質特性向上と共に、同様な用途の冷延鋼板の
代替材として使用可能になるために、多大のメリットが
ある。その方法の一つである、潤滑圧延法は、高いr平
均値が得られ、絞り性も冷延鋼板と比較しても高い部類
にある。しかし、この鋼板の製造には、低温加熱、α域
圧延、高潤滑等、これまでのラインに対し多大の負荷を
かけることになり、生産効率を悪化させる原因になって
いた。[Operation] Improving the r average value of a corrosion-resistant hot-rolled steel sheet has many advantages, since it not only improves the material properties of the steel sheet, but also allows it to be used as a substitute for cold-rolled steel sheets for similar purposes. One of the methods, the lubrication rolling method, provides a high average value of r and also has high drawability compared to cold rolled steel sheets. However, the production of this steel plate requires low-temperature heating, α-region rolling, high-level lubrication, etc., which places a large load on conventional lines, causing a deterioration in production efficiency.
【0014】まず第1に、本発明者らは、これらの問題
点を解決するため、■通常の熱延工程を高r平均値熱延
鋼板製造のための前工程(準備工程)に位置づけし、生
産障害を出さない条件の製造方法の検討。■負荷の大き
いα域潤滑圧延は後工程として位置づけ、専用のライン
としての生産方法の検討。■■と■の分化を最大に生か
して生産効率の向上と製品の特性向上を計る検討。■さ
らに、熱延鋼板用めっきラインとの連続化を考え、熱的
に省エネ、省工程が可能な連続ラインの検討を重ね、通
常の熱延工程を生産障害なく稼働するためには、加熱温
度を1100〜1200℃の範囲とし、仕上げ圧延温度
はAr3変態点以上で完了した後巻取る必要がある等の
知見を得た。First of all, in order to solve these problems, the present inventors positioned the normal hot rolling process as a pre-process (preparation process) for producing high r average value hot-rolled steel sheets. , Examination of manufacturing methods under conditions that do not cause production problems. ■ Position α-region lubrication rolling, which has a large load, as a subsequent process, and consider production methods as a dedicated line. Examining ways to improve production efficiency and product characteristics by making the most of the differentiation between ■■ and ■. ■Furthermore, in consideration of continuity with the plating line for hot-rolled steel sheets, we have repeatedly considered a continuous line that can thermally save energy and process, and in order to operate the normal hot-rolling process without production failure, It was found that it is necessary to set the temperature in the range of 1100 to 1200° C., and to complete the finish rolling at a temperature higher than the Ar3 transformation point before winding.
【0015】第2に、本発明者等は、高r平均値熱延鋼
板を熱延仕上げ工程で作り込んだ後、熱延から巻取り後
の高い鋼板温度に着目し、その熱を利用してめっき用金
属を粉末で該鋼板に吹き付けて溶融させ、そこにみられ
る合金反応を活用してめっき層を形成することを前提に
以下の実験を行い、後述する知見を得た。[0015] Second, the inventors focused on the high steel plate temperature after hot rolling and coiling after producing a high r average value hot rolled steel plate in the hot rolling finishing process, and utilized that heat. The following experiment was conducted on the premise that a powdered plating metal was sprayed onto the steel plate and melted, and the alloy reaction observed therein was utilized to form a plating layer, and the findings described below were obtained.
【0016】以下に条件限定について詳細に記す。
(1)鋼板化学成分
本発明において、鋼板化学成分の限定は、熱延材質すな
わち深絞り性(r平均値)を高くするために規制される
。本発明で適用するα域圧延法で、深絞り性を向上させ
るためには、深絞り性に有効な結晶方位、{111}面
強度比を増加し、有害な{100}面強度比を低減する
ため、熱延前の鋼板中の固溶C,Nを低減する必要があ
る。そのためには、C≦0.05%,N≦0.01%と
する必要がある。しかし、工業的に可能な下限は略10
ppm 程度である。更にC,Nを極微量まで低減させ
ることは不可避的にコストが増大する。[0016] The condition limitations will be described in detail below. (1) Chemical composition of steel sheet In the present invention, the chemical composition of steel sheet is limited in order to improve the hot rolling material, that is, the deep drawability (r average value). In order to improve deep drawability in the α region rolling method applied in the present invention, it is necessary to increase the crystal orientation and {111} plane strength ratio, which are effective for deep drawability, and reduce the harmful {100} plane strength ratio. Therefore, it is necessary to reduce solid solution C and N in the steel sheet before hot rolling. For this purpose, it is necessary to satisfy C≦0.05% and N≦0.01%. However, the industrially possible lower limit is approximately 10
It is about ppm. Furthermore, reducing C and N to extremely small amounts inevitably increases costs.
【0017】このコストの増大を防止するため、本発明
ではNb,Tiを添加してC,Nを析出物の形で固定す
る。しかし、このNb,Tiの添加もコストを増大する
ためC,N量とのバランスを取る必要がある。従って、
本発明では、C/12+N/14≦1.2(Ti/48
+Nb/93)の式によって上記のバランスを取り、固
溶CとNを炭窒化物として十分固定し、固溶C,Nを減
少させて{111}/{100}比を向上させ、深絞り
性を向上させている。In order to prevent this increase in cost, in the present invention, Nb and Ti are added to fix C and N in the form of precipitates. However, since the addition of Nb and Ti also increases cost, it is necessary to balance them with the amounts of C and N. Therefore,
In the present invention, C/12+N/14≦1.2(Ti/48
+Nb/93) is used to balance the above, sufficiently fix the solid solution C and N as carbonitrides, reduce the solid solution C and N, improve the {111}/{100} ratio, and perform deep drawing. Improving sexuality.
【0018】また、0.4(Ti/48+Nb/93)
≦C/12+N/14の条件を設け、{111}/{1
00}比の向上が飽和して以降のNb,Tiの過剰な添
加を防ぎ、無用なコスト上昇を防止している。また、P
,S,Mnについては多すぎると軟質化及び延性の劣化
を起こすため、P≦0.03%,S≦0.035%,M
n≦0.5%とする。[0018] Also, 0.4 (Ti/48+Nb/93)
Set the condition of ≦C/12+N/14, {111}/{1
This prevents excessive addition of Nb and Ti after the improvement in the 00} ratio is saturated, thereby preventing unnecessary cost increases. Also, P
, S, and Mn cause softening and deterioration of ductility if they are too large, so P≦0.03%, S≦0.035%, Mn
Let n≦0.5%.
【0019】(2)圧延素材
従来の温間潤滑圧延法では圧延素材は熱延鋼板中の固溶
C,Nを減少するためにTi,Nbとの炭窒化物を析出
させた方がよく、析出しやすいように低温加熱で行う方
がよい。しかし、本発明では、それに伴う生産効率の悪
化をさけ、巻取り工程で析出を狙うため、圧延素材条件
の限定はなく、通常の連続鋳造スラブ、薄肉の連続鋳造
スラブ、ダイレクトローリング法等の適用も可能である
。(2) Rolling material In the conventional warm lubrication rolling method, it is better for the rolling material to precipitate carbonitrides with Ti and Nb in order to reduce solid solution C and N in the hot rolled steel sheet. It is better to heat at a low temperature to facilitate precipitation. However, in the present invention, in order to avoid the accompanying deterioration in production efficiency and aim for precipitation in the winding process, there are no limitations on the rolling material conditions, and ordinary continuous casting slabs, thin-walled continuous casting slabs, direct rolling methods, etc. are applied. is also possible.
【0020】(3)熱間圧延条件
細粒のフェライトを得るには、仕上げ圧延温度を850
〜950℃とするのが望ましい。圧下率については特に
限定しないが、仕上げ全体の圧下率及び後半の圧下率を
高めることで更に細粒を得られることは言うまでもない
。(3) Hot rolling conditions To obtain fine-grained ferrite, the finish rolling temperature should be set at 850°C.
It is desirable to set the temperature to 950°C. The rolling reduction rate is not particularly limited, but it goes without saying that finer grains can be obtained by increasing the rolling reduction rate for the entire finishing process and the rolling reduction rate for the latter half.
【0021】(4)巻取り温度条件
本発明の手段の中で最も重要な巻取り温度は800〜7
00℃の温度とする。従来は、圧延前に炭窒化物を析出
させるためには加熱工程での析出を利用していた。その
ためには低温加熱が必要となり、上述したように不可避
的に生産効率が悪化していた。本発明では炭窒化物の析
出を最も早い高温巻取り工程で行うので、低温加熱は不
要となり、生産性の悪化は生じない。(4) Winding temperature condition The most important winding temperature among the means of the present invention is 800 to 7
The temperature shall be 00°C. Conventionally, precipitation in a heating process has been used to precipitate carbonitrides before rolling. For this purpose, low-temperature heating is required, and as mentioned above, production efficiency inevitably deteriorates. In the present invention, precipitation of carbonitrides is carried out in the earliest high-temperature winding process, so low-temperature heating is unnecessary and productivity does not deteriorate.
【0022】(5)温間圧延条件
これに続く温間圧延工程は、高温巻取りの顕熱を利用す
るため、従来のようにα域圧延を行うための仕上げ圧延
前での待ちによる時間ロスは生じない。巻取り後にその
まま圧延を行うことも可能であり、また所定温度になっ
たコイルを選択して圧延を行うことも可能である。(5) Warm rolling conditions The following warm rolling process utilizes the sensible heat of high-temperature coiling, so there is no time loss due to waiting before finishing rolling to perform α range rolling as in the past. does not occur. It is possible to perform rolling as is after winding, or it is also possible to select a coil that has reached a predetermined temperature and perform rolling.
【0023】一般に圧延前に、鋼板中の固溶C,Nがな
い状態でフェライト域で圧延を行うとr平均値を向上さ
せる{111}面強度が増加する。しかし、通常の圧延
では板厚の中心相の{111}は発達するが、表層は、
剪断歪の影響によって{110}が発達し、r平均値の
向上を阻害する。したがって、それを防止するために、
高r平均値熱延鋼板を製造する場合は、低温で潤滑を施
しつつ圧延を行う。Generally, if rolling is performed in the ferrite region in the absence of solid solution C and N in the steel sheet before rolling, the {111} plane strength, which improves the r average value, will increase. However, in normal rolling, the central phase {111} of the plate thickness develops, but the surface layer
{110} develops due to the influence of shear strain, which inhibits the improvement of the r average value. Therefore, to prevent it,
When producing a hot-rolled steel sheet with a high r average value, rolling is performed at low temperature while being lubricated.
【0024】この時、圧延仕上げ温度が低いほど中心層
の{111}の発達は大きくなるが低すぎると圧延負荷
が大きくなり、圧延に支障を来すことになる。圧延温度
がα域の高温領域では回復が早く、歪の蓄積が少なくな
り、{111}面強度は低下する。従って仕上げ圧延工
程でのα域の歪を多く蓄積させるために最終仕上げ温度
の上限は800℃とした。以上より熱延仕上げ圧延温度
範囲は圧延温度600〜800℃とした。[0024] At this time, the lower the rolling finish temperature, the greater the development of {111} in the center layer, but if it is too low, the rolling load will increase, which will impede rolling. When the rolling temperature is in the high temperature range α, recovery is rapid, accumulation of strain is reduced, and {111} plane strength is reduced. Therefore, the upper limit of the final finishing temperature was set at 800° C. in order to accumulate a large amount of strain in the α region during the finishing rolling process. From the above, the hot rolling finish rolling temperature range was set to 600 to 800°C.
【0025】また、本発明者らは、引続く金属粉噴射に
よるめっきを行うと、熱延工程で潤滑圧延を施さなくと
も高いr平均値を得られることを発見した。この原因は
、明確ではないが、表面への溶射めっき処理によって表
層に合金層ができる際に、r平均値向上に悪影響を及ぼ
す{110}の多い剪断層が消失してしまうためと考え
られる。従って、温間圧延材にめっき処理を施す場合に
は、潤滑は施さなくともよい。
(6)ドライデスケーリング条件
また、めっきの前処理としては、めっき層と地鉄との間
にスケールがあるとその部分で剥がれ易くなり、めっき
密着性が悪化するのでそれを防止するためにスケール除
去することと、地鉄とめっき層との接触面積を拡大して
合金化反応を促進するための鋼板表面の粗度の適性化と
を同時に行うことが良い。The present inventors have also discovered that by plating by subsequent metal powder injection, a high r average value can be obtained without lubricating rolling in the hot rolling process. The reason for this is not clear, but it is thought that when an alloy layer is formed on the surface by thermal spray plating on the surface, the shear layer with a lot of {110}, which has a negative effect on improving the r average value, disappears. Therefore, when plating a warm rolled material, it is not necessary to lubricate it. (6) Dry descaling conditions Also, as a pretreatment for plating, if there is scale between the plating layer and the base metal, it will be easy to peel off in that area and the plating adhesion will deteriorate, so in order to prevent It is preferable to simultaneously remove the metal and optimize the roughness of the steel sheet surface in order to increase the contact area between the base steel and the plating layer and promote the alloying reaction.
【0026】それには高圧水デスケーリングや液体を用
いないドライデスケーリングが良く、ドライデスケーリ
ングについて具体的なドライデスケーリングの方法とし
ては真空アーク(10−4〜10−6Torr)、プラ
ズマ、還元反応、磁性研磨(数十ミクロン〜数百ミクロ
ンの磁性粉を使用)、ショットブラスト、サンドブラス
ト、グリットブラスト、ワイヤーブラシ、グラインダー
等を単独ないしは組合せて利用することができる。ただ
し、高圧水デスケーリングの場合、デスケーリング後に
鋼板上に水が残っていると新たなスケールの発生を促進
し、更に粉末噴射時の合金化反応を妨げるので、デスケ
ーリング直後に高圧水または高圧ガスにより、十分な水
切りを行う必要がある。High-pressure water descaling or dry descaling that does not use a liquid is good for this. Specific dry descaling methods include vacuum arc (10-4 to 10-6 Torr), plasma, and reduction reaction. , magnetic polishing (using magnetic powder of several tens of microns to several hundred microns), shot blasting, sand blasting, grit blasting, wire brush, grinder, etc. can be used alone or in combination. However, in the case of high-pressure water descaling, if water remains on the steel plate after descaling, it will promote the generation of new scale and further impede the alloying reaction during powder injection. It is necessary to drain the water sufficiently using gas.
【0027】デスケーリング時に形成する鋼板の表面粗
度については、表面粗度が粗い方が表面積が大きくなり
合金化反応を起こし易いので、めっき密着性向上のため
に好ましい。鋼板の表面粗度がめっき密着性に与える影
響を調べるため、粒度150メッシュ以上のZn粉末ま
たはAl粉末を、該金属の融点よりも30〜200℃高
い温度に加熱した粗度調整済みの鋼板に噴射する実験を
行った。Regarding the surface roughness of the steel plate formed during descaling, the rougher the surface roughness, the larger the surface area and the easier the alloying reaction to occur, so it is preferable for improving plating adhesion. In order to investigate the effect of the surface roughness of a steel plate on plating adhesion, Zn powder or Al powder with a particle size of 150 mesh or more was heated to a temperature 30 to 200 °C higher than the melting point of the metal on a roughness-adjusted steel plate. We conducted an experiment to spray the liquid.
【0028】図1はその結果の一例で、Zn粉末をその
融点より100℃高い鋼板に噴射した場合の実験結果を
示したものであるが、このようにRa値で0.5μm以
上あればBI評点(ボールインパクトテストによる評点
)で1が得られ、充分なめっき密着性が得られ0.3〜
0.4μmでも2が得られ、実用上問題ないことが判明
した。上記したBI評点は1が最もめっき密着性の良い
ことを示し、値が大きくなるほどめっき密着性が悪いこ
とを示す。加工用途の耐蝕性熱延鋼板としては、このB
I評点で1を得ることが最も望ましい。Figure 1 shows an example of the results, and shows the experimental results when Zn powder was injected onto a steel plate 100°C higher than its melting point. A score of 1 (score based on ball impact test) was obtained, and sufficient plating adhesion was obtained with a score of 0.3 to 1.
2 was obtained even at 0.4 μm, and it was found that there was no problem in practical use. As for the above-mentioned BI rating, 1 indicates the best plating adhesion, and the larger the value, the worse the plating adhesion. As a corrosion-resistant hot-rolled steel sheet for processing purposes, this B
An I rating of 1 is most desirable.
【0029】デスケーリング後の新たなスケールの生成
を防ぐために、デスケーリング直後に粉末を噴射する必
要がある。デスケーリングと粉末噴射との間をアルゴン
、窒素等の不活性ガス雰囲気、不活性ガスと水素の混合
雰囲気、水素雰囲気等の非酸化性もしくは還元性雰囲気
中に維持すれば更に望ましい。この場合、非酸化性もし
くは還元性雰囲気中でデスケーリング或いは粉末噴射を
実施してもよいことは言うまでもない。[0029] In order to prevent the formation of new scale after descaling, it is necessary to inject powder immediately after descaling. It is more preferable to maintain a non-oxidizing or reducing atmosphere between descaling and powder injection, such as an inert gas atmosphere such as argon or nitrogen, a mixed atmosphere of an inert gas and hydrogen, or a hydrogen atmosphere. In this case, it goes without saying that descaling or powder injection may be carried out in a non-oxidizing or reducing atmosphere.
【0030】(7)めっき溶射条件
発明者等は、種々の温度まで加熱した熱延鋼板のスケー
ルを除去した後、純亜鉛粉末、純アルミニウム粉末、亜
鉛とアルミニウムの合金粉末など種々の金属粉末を噴射
する実験を行い、鋼板の温度が噴射する金属粉末の融点
よりも30℃以上高い場合に、密着性の良いめっき層を
形成することが可能であり、また鋼板の温度が該融点よ
りも200℃を超える温度になると酸化層が発達して外
観を損ない、まためっき量を制御できなくなることを見
出した。(7) Plating thermal spraying conditions After removing scale from hot rolled steel sheets heated to various temperatures, the inventors applied various metal powders such as pure zinc powder, pure aluminum powder, and zinc-aluminum alloy powder. A spraying experiment was conducted, and it was found that if the temperature of the steel plate was 30°C or more higher than the melting point of the metal powder to be sprayed, it was possible to form a plating layer with good adhesion. It was discovered that when the temperature exceeds ℃, an oxidized layer develops, impairing the appearance, and making it impossible to control the amount of plating.
【0031】これ等の知見から、金属粉末の噴射を受け
る鋼板の温度を粉末の融点よりも30〜200℃の範囲
に高くすると、粉末を溶かす融解熱と、合金反応を起こ
すために十分な時間溶融状態を維持する熱が供給され酸
化層の発達も防止できることが判明した。Based on these findings, if the temperature of the steel plate to which the metal powder is injected is raised to a range of 30 to 200°C above the melting point of the powder, the heat of fusion to melt the powder and the sufficient time to cause the alloy reaction will be generated. It has been found that heat is supplied to maintain the molten state and the development of an oxidized layer can also be prevented.
【0032】耐蝕用途のめっき層を形成する金属として
は、亜鉛、アルミニウム、鉛、亜鉛とアルミニウムの合
金、鉄の含有量が5重量%以下程度の亜鉛と鉄の合金等
がある。これらの金属の融点は327℃以上で約700
℃以下程度の温度範囲にあり、これ等の融点よりも30
〜200℃高い温度範囲は、熱間圧延工程では仕上げ圧
延終了から巻取りまでの間にあり、その間で噴射に使用
する金属の融点を基に生産性と経済性の良い位置を噴射
位置とすれば良い。[0032] Examples of metals forming a plating layer for corrosion-resistant purposes include zinc, aluminum, lead, an alloy of zinc and aluminum, and an alloy of zinc and iron with an iron content of about 5% by weight or less. The melting point of these metals is about 700℃ above 327℃.
It is in the temperature range of about ℃ or below, and is 30℃ higher than the melting point of these.
The temperature range of ~200℃ higher is the period from the end of finish rolling to the winding in the hot rolling process, and during that time, the injection position is determined to be the most productive and economical position based on the melting point of the metal used for injection. Good.
【0033】また、吹き付ける金属粉末の粒度について
は、あまり粉末が大きいと熱伝導が悪く溶融し難くなる
ため、飛散消耗せず、多大の微粉化費を要しない範囲で
小さい粉末の方が良い。金属粉末の粒度がめっき密着性
に与える影響を調べるため、Zn粉末またはAl粉末を
、該金属の融点よりも30〜200℃高い温度に加熱し
た表面粗度をRa値で0.5μm以上に調整済みの鋼板
に噴射する実験を行った。Regarding the particle size of the metal powder to be sprayed, if the powder is too large, heat conduction will be poor and it will be difficult to melt, so it is better to use a small powder as long as it does not scatter and consume and does not require a large amount of pulverization cost. In order to investigate the effect of metal powder particle size on plating adhesion, Zn powder or Al powder was heated to a temperature 30 to 200 ° C higher than the melting point of the metal and the surface roughness was adjusted to an Ra value of 0.5 μm or more. An experiment was conducted in which the liquid was sprayed onto a finished steel plate.
【0034】図2はその結果の一例で、Zn粉末をその
融点より100℃高い鋼板に噴射した場合の実験結果を
示したものであるが、このように粉末の粒度が150メ
ッシュ以上あれば迅速的確に溶融して、BI評点で1が
得られめっき密着性が良好となり50以上150メッシ
ュ未満でもBI評点で2が得られ、実用上問題とならな
い密着性が得られることが判明した。Figure 2 shows an example of the results, and shows the experimental results when Zn powder was injected onto a steel plate 100°C higher than its melting point. It was found that it was melted accurately and a BI rating of 1 was obtained, resulting in good plating adhesion, and that even when the mesh was 50 or more and less than 150 mesh, a BI rating of 2 was obtained, and adhesion that did not pose any practical problems could be obtained.
【0035】[0035]
【実施例】表1に供試材の化学成分と熱延条件を示す。
表1の各材料は、熱間圧延−巻取り後に温間圧延を実施
し、その温間圧延機とその後の巻取り機との間に種々の
ドライデスケーリング装置と粉末噴射装置を隣接し、そ
の間は各種の雰囲気として、温間圧延後の鋼板に種々の
ドライデスケーリング装置でスケール除去と粗度調整を
行った後、粉末噴射装置で金属粉末を噴射してから巻取
った。その際の各条件とめっき密着性、耐蝕性及びめっ
き後のr平均値を表2に示す。[Example] Table 1 shows the chemical composition and hot rolling conditions of the test materials. Each material in Table 1 is prepared by performing warm rolling after hot rolling and winding, and placing various dry descaling devices and powder injection devices adjacent to each other between the warm rolling mill and the subsequent winding machine. During this time, various atmospheres were maintained, and after the steel plate after warm rolling was subjected to scale removal and roughness adjustment using various dry descaling devices, metal powder was injected using a powder injection device, and the sheet was wound up. Table 2 shows each condition, plating adhesion, corrosion resistance, and average r value after plating.
【0036】[0036]
【表1】[Table 1]
【0037】[0037]
【表2】[Table 2]
【0038】[0038]
【表3】[Table 3]
【0039】[0039]
【表4】[Table 4]
【0040】表2に示したように本発明例のNo.1〜
14は、めっき密着性がよく、耐蝕性も良好で、r平均
値も1.4以上を有する深絞り性に優れる耐蝕性熱延鋼
板を得ることができた。これに対し本発明の要件である
粉末の粒度が外れたNo.16、鋼板の表面粗度が外れ
たNo.17、鋼板の下限温度が外れたNo.18,2
1、鋼板の上限温度が外れたNo.19,23の各比較
例は共にめっき密着性が悪く、所要の耐蝕性を有する耐
蝕性熱延鋼板を得ることはできなかった。また、No.
22は温間圧延温度が800℃以上のために{111}
面強度の発達が妨げられ、No.20は、巻取り温度が
低かったために、炭窒化物の析出が不十分で固溶C,N
が固着できなかったため、No.15は溶射等の条件は
満たしているので、めっき密着性、耐蝕性は良好なもの
のTi,Nb無添加のため、固溶C,Nが固着できない
ためいずれも1.4以上の高いr平均値は得られなかっ
た。As shown in Table 2, the present invention example No. 1~
In No. 14, it was possible to obtain a corrosion-resistant hot-rolled steel sheet with good plating adhesion, good corrosion resistance, and excellent deep drawability with an r average value of 1.4 or more. On the other hand, No. 1, which does not have the particle size of the powder that is a requirement of the present invention. 16. No. 1 whose surface roughness of the steel plate was off. 17. No. 1 where the lower limit temperature of the steel plate was exceeded. 18,2
1. No. 1 where the upper limit temperature of the steel plate was exceeded. Comparative Examples Nos. 19 and 23 both had poor plating adhesion, and it was not possible to obtain a corrosion-resistant hot-rolled steel sheet having the required corrosion resistance. Also, No.
22 is {111} because the warm rolling temperature is 800℃ or higher.
The development of surface strength was hindered, and No. In No. 20, because the winding temperature was low, precipitation of carbonitrides was insufficient and solid solution C, N
Because it could not be fixed, No. No. 15 satisfies the conditions such as thermal spraying, so the plating adhesion and corrosion resistance are good, but since no Ti or Nb is added, solute C and N cannot stick, so all have high r average values of 1.4 or more. was not obtained.
【0041】なおNo.4,5は圧延時の潤滑の必要性
を見るために、高潤滑油使用の有無を除き、いずれもほ
ぼ同じ条件で製造したものであるが、ほぼ同じ値のr平
均値が得られ、溶射めっき鋼板では無潤滑圧延材でも高
いr平均値が得られた。[0041] Note that No. 4 and 5 were manufactured under almost the same conditions, except for the use of high-quality lubricating oil, in order to examine the necessity of lubrication during rolling, and almost the same r average value was obtained. A high average value of r was obtained for the plated steel sheet even when rolled without lubrication.
【0042】[0042]
【発明の効果】本発明によると、通常熱延工程ラインの
生産性を下げることなく亜鉛、アルミニウム、鉛等の単
一金属或いはその合金等のめっき層を有し、さらに高い
絞り性を有する耐蝕性熱間圧延鋼板を、小規模の設備で
円滑、安定してめっき密着性よく生産性よく、経済的に
製造することが可能となるので、当業分野にもたらす工
業的効果は極めて大きい。[Effects of the Invention] According to the present invention, a corrosion-resistant material having a plating layer of a single metal such as zinc, aluminum, or lead or an alloy thereof without reducing the productivity of a normal hot rolling process line and having high drawability. This makes it possible to economically produce hot-rolled steel sheets with high plating adhesion, smoothly, stably, with good plating adhesion, and with good productivity using small-scale equipment, so the industrial effect brought about in the field of art is extremely large.
【図1】めっき金属の粉末を吹き付ける前の鋼板の表面
粗度をRa値とBI評点で示しためっき密着性の関係を
2水準の粉末粒度で示す図表である。FIG. 1 is a chart showing the relationship between the surface roughness of a steel plate before being sprayed with plating metal powder in terms of Ra value and plating adhesion in terms of BI rating using two levels of powder particle size.
【図2】めっき金属の粉末の粒度とBI評点で示しため
っき密着性の関係を2水準の表面粗度Ra値で示す図表
である。FIG. 2 is a chart showing the relationship between the particle size of the plating metal powder and the plating adhesion indicated by the BI rating using two levels of surface roughness Ra values.
Claims (2)
0.01%以下、C及びNの含有量と、Ti及びNbの
一方或いは両方の含有量が、0.4(Ti/48+Nb
/93)≦C/12+N/14≦1.2(Ti/48+
Nb/93)の関係にある熱延鋼板用鋼を、Ar3変態
点以上で熱間圧延を終了した後、700〜800℃で巻
取りを行い、引続き600〜800℃で圧延を行った後
に鋼板を巻取るまでの間に、該鋼板表面のスケールをド
ライデスケーリングまたは高圧水デスケーリングを用い
て除去し、引続き、亜鉛、アルミニウム、鉛等の単一金
属或いはその合金等の金属粉末を前記鋼板の所要の面に
前記金属粉末の融点よりも30℃以上200℃以下の範
囲に高い鋼板温度において噴射して、該鋼板の所要の面
に溶融めっき層を形成することを特徴とする耐蝕性熱間
圧延鋼板の製造方法。[Claim 1] In weight%, C: 0.05% or less, N:
0.01% or less, the content of C and N and the content of one or both of Ti and Nb is 0.4 (Ti/48+Nb
/93)≦C/12+N/14≦1.2(Ti/48+
Nb/93) After completing hot rolling at the Ar3 transformation point or higher, coiling is performed at 700 to 800°C, and after rolling at 600 to 800°C, the steel plate is prepared. Before winding the steel sheet, scale on the surface of the steel sheet is removed using dry descaling or high-pressure water descaling, and then metal powder such as a single metal such as zinc, aluminum, lead, or an alloy thereof is applied to the steel sheet. Corrosion-resistant heat is sprayed onto a desired surface of the steel sheet at a temperature higher than the melting point of the metal powder in a range of 30° C. to 200° C. to form a hot-dip coating layer on the desired surface of the steel sheet. A method for producing inter-rolled steel plates.
リングまたは高圧水デスケーリングを用いて除去すると
共に、表面粗度をRa値で0.5μm以上とし、引続き
亜鉛、アルミニウム、鉛等の単一金属或いはその合金等
の粒度150メッシュ以上の金属粉末を前記鋼板の所要
の面に前記金属粉末の融点よりも30℃以上200℃以
下の範囲に高い鋼板温度において噴射して、該鋼板の所
要の面に溶融めっき層を形成することを特徴とする請求
項1に記載する耐蝕性熱間圧延鋼板の製造方法。[Claim 2] Scale on the surface of the steel plate is removed using dry descaling or high-pressure water descaling, and the surface roughness is set to 0.5 μm or more in terms of Ra value, and then a single metal such as zinc, aluminum, lead, etc. A metal powder such as an alloy having a particle size of 150 mesh or more is injected onto a required surface of the steel plate at a steel plate temperature higher than the melting point of the metal powder in a range of 30°C or more and 200°C or less. The method for producing a corrosion-resistant hot-rolled steel sheet according to claim 1, further comprising forming a hot-dip plating layer.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP3116197A JPH04346626A (en) | 1991-05-21 | 1991-05-21 | Manufacture of corrosion resistant hot rolled steel sheet high in productive efficiency and excellent in deep drawability |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP3116197A JPH04346626A (en) | 1991-05-21 | 1991-05-21 | Manufacture of corrosion resistant hot rolled steel sheet high in productive efficiency and excellent in deep drawability |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH04346626A true JPH04346626A (en) | 1992-12-02 |
Family
ID=14681243
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP3116197A Withdrawn JPH04346626A (en) | 1991-05-21 | 1991-05-21 | Manufacture of corrosion resistant hot rolled steel sheet high in productive efficiency and excellent in deep drawability |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH04346626A (en) |
-
1991
- 1991-05-21 JP JP3116197A patent/JPH04346626A/en not_active Withdrawn
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