JPS63128168A - Production of alloyed and zinc plated steel sheet having excellent deep drawability - Google Patents
Production of alloyed and zinc plated steel sheet having excellent deep drawabilityInfo
- Publication number
- JPS63128168A JPS63128168A JP27297586A JP27297586A JPS63128168A JP S63128168 A JPS63128168 A JP S63128168A JP 27297586 A JP27297586 A JP 27297586A JP 27297586 A JP27297586 A JP 27297586A JP S63128168 A JPS63128168 A JP S63128168A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- plating
- alloyed
- steel sheet
- temp
- 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.)
- Granted
Links
- 229910000831 Steel Inorganic materials 0.000 title abstract description 32
- 239000010959 steel Substances 0.000 title abstract description 32
- 239000011701 zinc Substances 0.000 title abstract description 8
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 title abstract description 7
- 229910052725 zinc Inorganic materials 0.000 title abstract description 7
- 238000004519 manufacturing process Methods 0.000 title description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 37
- 229910000655 Killed steel Inorganic materials 0.000 claims abstract description 31
- 229910052742 iron Inorganic materials 0.000 claims abstract description 17
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 239000010936 titanium Substances 0.000 claims description 14
- 229910001335 Galvanized steel Inorganic materials 0.000 claims description 6
- 239000008397 galvanized steel Substances 0.000 claims description 6
- 238000010438 heat treatment Methods 0.000 claims description 4
- CYKMNKXPYXUVPR-UHFFFAOYSA-N [C].[Ti] Chemical compound [C].[Ti] CYKMNKXPYXUVPR-UHFFFAOYSA-N 0.000 claims description 2
- 238000000034 method Methods 0.000 claims description 2
- 238000007747 plating Methods 0.000 abstract description 37
- 238000005275 alloying Methods 0.000 abstract description 17
- 238000000227 grinding Methods 0.000 abstract description 9
- 238000007740 vapor deposition Methods 0.000 abstract description 7
- 238000000137 annealing Methods 0.000 abstract description 4
- 229910052799 carbon Inorganic materials 0.000 abstract description 4
- 238000009792 diffusion process Methods 0.000 abstract description 2
- 230000002950 deficient Effects 0.000 abstract 1
- 239000010410 layer Substances 0.000 description 29
- 239000000758 substrate Substances 0.000 description 14
- 229910045601 alloy Inorganic materials 0.000 description 10
- 239000000956 alloy Substances 0.000 description 10
- 238000005246 galvanizing Methods 0.000 description 4
- 230000001590 oxidative effect Effects 0.000 description 4
- 238000007738 vacuum evaporation Methods 0.000 description 4
- 230000007423 decrease Effects 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- 238000000576 coating method Methods 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000009833 condensation Methods 0.000 description 2
- 230000005494 condensation Effects 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 238000012546 transfer Methods 0.000 description 2
- 238000001771 vacuum deposition Methods 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 238000000151 deposition Methods 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 210000003746 feather Anatomy 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 238000007789 sealing Methods 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 238000004804 winding Methods 0.000 description 1
Landscapes
- Physical Vapour Deposition (AREA)
Abstract
Description
【発明の詳細な説明】
[技術分野]
本発明は深絞り性に優れ、かつ耐パウダリング性に優れ
た合金化蒸着亜鉛メッキ鋼板を製造する方法に関する。DETAILED DESCRIPTION OF THE INVENTION [Technical Field] The present invention relates to a method for producing an alloyed vapor-deposited galvanized steel sheet having excellent deep drawability and powdering resistance.
[従来技術]
一般に深絞り加工用鋼板としてA文ギルド鋼およびTi
キルド鋼が知らている。ところでTiキルド鋼をベース
とした合金化蒸着亜鉛メッキ鋼板はAfLキルド鋼と同
条件で合金化処理した場合、加工時にメッキ層のフレー
キングを生じ易い問題がある。この原因はTiキルド鋼
はAMギルド鋼・等に比べて鋼中の鉄がメッキ層に拡散
し易く、メッキ層中の平均鉄濃度が過剰になるためであ
ると考えられる。Tiキルド鋼とAnキルド鋼について
蒸着亜鉛メッキを施し、その後、メッキ層表面まで合金
化゛した場合、亜鉛メッキ層中の鉄の濃度勾配の一例を
第1図に示す0図示されるAnキルド鋼ではメッキ表面
からメッキ層の深部にかけて鉄濃度が約5−6.5%で
あり、該メッキ層深部から鋼板との界面の間で鉄濃度勾
配が急激に上昇している。一方、Tiキルド鋼では1表
層付近の鉄濃度はA9.ギルド鋼と同じ5〜6zである
が。[Prior art] Generally, A-shaped guild steel and Ti steel are used as steel sheets for deep drawing.
Killed steel is known. By the way, when an alloyed vapor deposited galvanized steel sheet based on Ti killed steel is alloyed under the same conditions as AfL killed steel, there is a problem in that the plated layer tends to flake during processing. The reason for this is thought to be that iron in the Ti-killed steel diffuses into the plating layer more easily than in the AM guild steel, and the average iron concentration in the plating layer becomes excessive. An example of the iron concentration gradient in the galvanized layer is shown in Figure 1 when vapor deposited galvanizing is applied to Ti killed steel and An killed steel, and then alloyed to the surface of the plated layer. In this case, the iron concentration is about 5-6.5% from the plating surface to the deep part of the plating layer, and the iron concentration gradient increases rapidly from the deep part of the plating layer to the interface with the steel plate. On the other hand, in Ti-killed steel, the iron concentration near the first surface layer is A9. It's the same 5~6z as Guild Steel.
メッキ層中間部から深部にかけての鉄濃度が、AIギル
ド鋼に比べ高くなっている。このようにTiギルド鋼は
A交キルド鋼に比べ、鉄濃度の高い合金化メッキ層を有
することが分る。このため、蒸着亜鉛メッキされたTi
キルド鋼をA見キルド鋼と同条件で合金化処理を行なう
と合金化が過度に進行し、メッキ層中の平均鉄濃度がA
nキルド鋼の場合より 1.5〜2.0%高くなり、平
均鉄濃度が過剰となる結果、耐パウダリング性が低下し
加工時にメッキ層が剥離損傷し易くなる問題がある。The iron concentration from the middle to the deep part of the plating layer is higher than that of AI guild steel. It can thus be seen that the Ti-guild steel has an alloyed plating layer with a higher iron concentration than the A-cross-killed steel. For this reason, the evaporated galvanized Ti
If killed steel is alloyed under the same conditions as killed steel, alloying will proceed excessively and the average iron concentration in the plating layer will be A.
The iron concentration is 1.5 to 2.0% higher than that of n-killed steel, resulting in an excessive average iron concentration, resulting in a problem that the powdering resistance decreases and the plating layer is easily damaged by peeling during processing.
[問題解決の知見]
本発明者等は1以上のようにTiキルド鋼に合金化蒸着
亜鉛メッキを施す場合に、A立キルド鋼と同条件で合金
化処理を施すと合金化が過度に進行し、耐パウダリング
性が低下する問題のあることを見出し、この問題を解消
する方法として、低炭素Tiキルド鋼について、その蒸
着メッキ直前の基板温度を出来るだけ低く維持し、かつ
合金化温度と時間を所定の範囲に制限することにより。[Knowledge for solving the problem] The present inventors found that when alloying vapor deposited galvanizing is applied to Ti-killed steel as described in 1. above, alloying progresses excessively when the alloying treatment is performed under the same conditions as A-stand killed steel. However, we discovered that there was a problem of reduced powdering resistance, and as a way to solve this problem, we tried to maintain the substrate temperature as low as possible immediately before vapor deposition plating for low carbon Ti killed steel, and to maintain the temperature of the substrate as low as possible just before the vapor deposition plating, and to reduce the alloying temperature. By limiting the time to a predetermined range.
合金層中の平均Fe濃度を8.0〜12.0重量%に制
御すれば、耐パウダリング性の良好な合金化亜鉛メッキ
Tiキルド鋼を得ることが出来る知見を得た。We have found that by controlling the average Fe concentration in the alloy layer to 8.0 to 12.0% by weight, it is possible to obtain alloyed galvanized Ti killed steel with good powdering resistance.
本発明によれば、低炭素チタンキルド鋼(C≦o、ot
o重Wig 、 S i <0.15i4% 、 M
n : 0.15〜0.85重ffi$ 、 T i
: 0.05〜0.30重i%および不可避的不純物
トシテP≦0.020重量$ 、S≦0.020重J1
% 、 5oIAl≦0.050重iB)を蒸着亜鉛メ
ッキする際、メッキ直前の鋼板温度を180〜280℃
に設定し、その後、バッチ焼鈍炉内で非酸化性雰囲気で
220〜320℃、1〜50時間加熱することにより、
鉄濃度が8.0〜12.0重量%の合金化メッキ層を有
する合金化亜鉛メッキ鋼板を製造することを特徴とする
方法が提供される。According to the present invention, low carbon titanium killed steel (C≦o, ot
o WeightWig, S i <0.15i4%, M
n: 0.15-0.85 ffi$, Ti
: 0.05 to 0.30 weight i% and unavoidable impurities P≦0.020 weight $, S≦0.020 weight J1
%, 5oIAl≦0.050weight iB), the steel plate temperature immediately before plating is set at 180 to 280℃.
and then heated in a non-oxidizing atmosphere in a batch annealing furnace at 220-320°C for 1-50 hours.
A method is provided, characterized in that it produces an alloyed galvanized steel sheet having an alloyed plated layer with an iron concentration of 8.0 to 12.0% by weight.
本発明においては、次の組成(重量%)を有する低炭素
Tiキルド鋼が用いられる。In the present invention, a low carbon Ti killed steel having the following composition (% by weight) is used.
深絞り用鋼板として用いられるTiキルド鋼は極低炭素
鋼であり、通常C≦o、oio重量%のものが用いられ
る。またSiはS i <0.15重量%が好ましい、
Siが0.15より多いと、メッキ密着性が低下する
。この密着性を向上させるには基板温度を上げる必要が
あるが、Tiキルド鋼の場合、Feの拡散が早く基板温
度を上げると、メッキ層と鋼板との界面に脆弱な合金層
が発生する問題が生じる。したがって、Tiキルド鋼の
Si含有量は0.15wt$以下が望ましい、Mnは主
に強度を高める成分であり、 0.15〜0.85重量
%が好ましい。Ti-killed steel used as a steel plate for deep drawing is an extremely low carbon steel, and usually has C≦o and oio weight %. Moreover, Si is preferably Si<0.15% by weight,
When Si is more than 0.15, plating adhesion decreases. In order to improve this adhesion, it is necessary to raise the substrate temperature, but in the case of Ti-killed steel, Fe diffuses quickly and when the substrate temperature is raised, a weak alloy layer is generated at the interface between the plating layer and the steel plate. occurs. Therefore, the Si content of the Ti-killed steel is preferably 0.15 wt$ or less, and Mn is a component that mainly increases strength, and is preferably 0.15 to 0.85 wt%.
0.15重着%より少ないと充分な強度が保たれず、他
方、0.85重量%を越えても、メッキ密着性その他の
品質上の問題は生じないが0.85wt$以上のMnを
含有しても、それ以上の強度の上昇は望めない。If the Mn content is less than 0.15 wt%, sufficient strength cannot be maintained; on the other hand, if it exceeds 0.85 wt%, no problems with plating adhesion or other quality will occur; Even if it is contained, no further increase in strength can be expected.
Tiは0.05〜0.30重量%である。これは通常の
深絞り用Tiキルド鋼と同程度の含有量である。Ti is 0.05 to 0.30% by weight. This content is comparable to that of ordinary Ti killed steel for deep drawing.
一般に深絞り用鋼板としてTiは鋼中のCを固定するた
めに通常Cの4倍量程度の含有量が必要であり、更に鋼
中の不純物としての窒素量を勘案し、上記含有量に定め
られる。Generally, in steel sheets for deep drawing, the content of Ti is required to be about four times the amount of normal C in order to fix C in the steel.Furthermore, taking into account the amount of nitrogen as an impurity in the steel, the above content is set. It will be done.
その他に、不可避的不純物としてP≦0.020重量%
、S≦0.020重量%、5olAI≦0.050重量
%が含まれる。これらは普通鋼の不純物レベルと同一で
ある。In addition, P≦0.020% by weight as unavoidable impurities
, S≦0.020% by weight, and 5olAI≦0.050% by weight. These are the same impurity levels as ordinary steel.
上記Tiキルド鋼について、メッキ直前の鋼板温度を1
80〜280℃に設定して蒸着亜鉛メッキを施す、一般
に蒸着亜鉛メッキにおいては、メッキ時の基板温度が低
く過ぎると亜鉛メッキ層の密着性が不良になるので通常
基板温度を180℃以上に保持する。他方、蒸着メッキ
においては亜鉛蒸気が鋼板表面に凝縮してメッキ層を形
成するので亜鉛の凝縮熱により基盤の温度が上昇する。Regarding the above Ti-killed steel, the temperature of the steel plate immediately before plating was set to 1
Vapor-deposited galvanizing is performed at a temperature of 80 to 280°C. Generally, in vapor-deposited galvanizing, if the substrate temperature during plating is too low, the adhesion of the galvanized layer will be poor, so the substrate temperature is usually kept at 180°C or higher. do. On the other hand, in vapor deposition plating, zinc vapor condenses on the surface of the steel sheet to form a plating layer, so the temperature of the base increases due to the heat of condensation of the zinc.
その他、蒸着室内の巻付ロールからの熱伝達も基板温度
を上昇させる要因となる。従ってメッキ直前の基板温度
が必要以上に高いと上記凝縮熱や熱伝達により一層基板
温度が上昇し、これに起因してメッキ層と鋼板との界面
付近に脆弱な合金層が発達してメー、キ層の密着性を損
なう問題を生じる。−例ではノー2キ後の鋼帯温度が3
60℃前後になると約35秒経過後に0.1〜1.0ル
の合金層が発達し、銅帯温度が410℃以上になると5
秒以下で上記層厚の合金層が発達する。このため上記合
金層の発達を防止するため、上記温度上昇を考慮しメッ
キ直前の鋼帯の基板温度を予め厚目付けの場合には18
θ〜280℃、薄目付けの場合には180〜300℃に
調整している。本発明においてはTiキルド鋼Aiキル
ド鋼に比べ、合金化しやすい為、更に通常の基板温度よ
り低く、厚目付けの場合に180〜260℃薄目付けの
場合に180〜280℃に調整し、鋼中からメッキ層へ
の鉄の拡散を最少限に抑える。In addition, heat transfer from the winding rolls in the deposition chamber is also a factor that increases the substrate temperature. Therefore, if the substrate temperature immediately before plating is higher than necessary, the substrate temperature will rise further due to the above-mentioned condensation heat and heat transfer, and this will cause a fragile alloy layer to develop near the interface between the plating layer and the steel plate. This causes a problem of impairing the adhesion of the layer. - In the example, the steel strip temperature after 2-ki is 3
When the temperature reaches around 60°C, an alloy layer of 0.1 to 1.0 liters develops after about 35 seconds, and when the copper strip temperature reaches 410°C or higher, an alloy layer of 0.1 to 1.0 l develops.
An alloy layer of the above thickness develops in seconds or less. Therefore, in order to prevent the development of the alloy layer, the substrate temperature of the steel strip immediately before plating should be adjusted to 18.
The temperature is adjusted to θ to 280°C, and 180 to 300°C in the case of a thin basis weight. In the present invention, since Ti-killed steel is easier to alloy than Ai-killed steel, the temperature of the substrate is lower than the normal substrate temperature, adjusted to 180-260℃ for thick coatings and 180-280℃ for thin coatings. Minimize diffusion of iron from the plated layer to the plated layer.
上記蒸着メッキの後に合金化処理を施す。After the vapor deposition plating described above, alloying treatment is performed.
一般にバッチ焼鈍による合金化処理としては、鋼板の酸
化を防止するため、非酸化性雰囲気で。Generally, batch annealing is performed in a non-oxidizing atmosphere to prevent oxidation of the steel plate.
lrJ熱処理を行なう、コイル形状はタイ!・コイル、
オープンコイルいずれの形状でもよい、処理温度、時間
はメッキ付着量、および目標F e rij率により変
更しうる。第2図に合金化処理のヒートサイクルを、第
3図に合金化処理範囲を示す、第2図のヒートサイクル
は合金化処理後、100℃以下まで炉内を非酸化性雰囲
気にて冷却した場合を示し、炉内の非酸化性雰囲気は、
N2をベースとし、それにN2を3〜75%含有した組
成をもつガスからなる。またガス中のCO,Co2e度
はいずれも0〜lotである。The coil shape is tied with lrJ heat treatment! ·coil,
Any shape of open coil may be used, and the processing temperature and time may be changed depending on the amount of plating deposited and the target F e rij rate. Figure 2 shows the heat cycle for alloying treatment, and Figure 3 shows the range of alloying treatment. In the heat cycle in Figure 2, after alloying treatment, the inside of the furnace was cooled to below 100°C in a non-oxidizing atmosphere. In this case, the non-oxidizing atmosphere in the furnace is
It consists of a gas having a composition based on N2 and containing 3 to 75% N2. Moreover, the CO and Co2e degrees in the gas are both 0 to a lot.
第3図は、Fe量率8′〜12%を含む合金化処理条件
の範囲を示し、図中、実線ab内の範囲はA文ギルド鋼
ベース、破t!cdでかこまれた点線領域がTiキルド
鋼ベースの場合を示す0合金化処理時間をlhr以上と
したのは、実験上それ以丁の均熱時間では、炉温か低下
しなかったためであり、又、50時間以下としたのは、
それ以上では生産性が向上しないためである。FIG. 3 shows the range of alloying treatment conditions including Fe content of 8' to 12%. The dotted line area surrounded by cd indicates the case of Ti-killed steel base.The reason why the alloying treatment time was set to 1hr or more was because the furnace temperature did not decrease with soaking time longer than 1hr in the experiment, and , 50 hours or less was set as
This is because productivity cannot be improved beyond that.
[実施例および比較例]
第4図に示す連続式真空蒸着亜鉛メッキ装置を用いてT
i キルド鋼に亜鉛メッキを施した。なお1図中1は鋼
板、2は前処理炉、3a、3bは真空シールロール室、
4a、4bは真空蒸着室、5は冷却室である。操業条件
を次表に示す。[Example and Comparative Example] T
i Killed steel is galvanized. In addition, in 1 figure, 1 is a steel plate, 2 is a pretreatment furnace, 3a, 3b is a vacuum seal roll chamber,
4a and 4b are vacuum deposition chambers, and 5 is a cooling chamber. The operating conditions are shown in the table below.
なお、片面メッキを施す場合には、第1真空蒸着メッキ
室4a、または第2真空蒸着メッキ室4bのいずれか一
方だけで真空蒸着Znメッキすればよい。In addition, when performing single-sided plating, vacuum evaporation Zn plating may be performed only in either the first vacuum evaporation plating chamber 4a or the second vacuum evaporation plating chamber 4b.
これらの真空蒸着Znメッキ鋼板をバッチ焼鈍炉中で加
熱し合金化処理し、合金化Znメッキ鋼板を製造した0
合金化処理条件を次表に示す。These vacuum-deposited Zn-plated steel sheets were heated and alloyed in a batch annealing furnace to produce alloyed Zn-plated steel sheets.
The alloying treatment conditions are shown in the table below.
付着量、基板温度、加熱温度、保持時間の組合せと製造
された鋼板の表面外観、加工性(#パウダリング性)を
調べた結果を第1表に示す、耐パウダリング性は6t、
180°曲げ、曲げ戻し後に内側のパウダリング発生
状況で評価した0次に、比較のため蒸着時の基板温度お
よび合金化時の加熱温度、保持時間を第2表に示す条件
に設定し、その他は実施例と同様にして亜鉛メッキの合
金化処理を行った。この結果を第2表に示す。Table 1 shows the results of examining the combinations of adhesion amount, substrate temperature, heating temperature, and holding time, as well as the surface appearance and workability (#powdering property) of the manufactured steel sheets.The powdering resistance was 6t,
After 180° bending and unbending, the powdering on the inside was evaluated. For comparison, the substrate temperature during vapor deposition, the heating temperature during alloying, and the holding time were set to the conditions shown in Table 2, and other conditions were set as shown in Table 2. Alloying treatment for zinc plating was carried out in the same manner as in the examples. The results are shown in Table 2.
第1表
第1表つづき
第2表
上記結果から明らかなように、本実施例の合金化亜鉛メ
ッキ鋼板はいずれも良好な表面外観と加工性を具えてい
るが、比較例のものは合金層中に亜鉛が残存し、あるい
は加工性に劣る。Table 1 Table 1 Continued Table 2 As is clear from the above results, the alloyed galvanized steel sheets of this example all have good surface appearance and workability, but the comparative example has an alloy layer. Zinc remains inside or the workability is poor.
[発明の効果]
本発明の製造方法によれば、チタンキルド鋼に合金化亜
鉛メッキを施す際、最適な鉄量率の合金化層を形成する
ことができ、表面外観、深絞り性および耐パウダリング
性に優れた合金化亜鉛メッキ鋼板を得ることができる。[Effects of the Invention] According to the manufacturing method of the present invention, when applying alloyed zinc plating to titanium killed steel, it is possible to form an alloyed layer with an optimal iron content ratio, and improve the surface appearance, deep drawability, and powder resistance. An alloyed galvanized steel sheet with excellent ring properties can be obtained.
第1図はチタンキルド鋼とアルミギルド鋼について合金
層中の鉄濃度を示すグラフ、第2図は合金化処理のヒー
トサイクルを示すグラフ、第3図は合金化時間と処理温
度との関係を示すグラフ、第4図は連褪式真空蒸着メッ
キ装置の一例を示す概略図である。
図面中 1−鋼板、2−前処理炉、3a、3b−真空シ
ール口−ル室、4a、4b−真空蒸着室。
5−冷却室
第1図
1“孟 (ノブA)f) 羽−石 G
仰り刃え)第2図
呵M Chr)
第3図
1 2 5 lO2050処y
L哨M(hr)Figure 1 is a graph showing the iron concentration in the alloy layer for titanium killed steel and aluminum guild steel, Figure 2 is a graph showing the heat cycle of alloying treatment, and Figure 3 is a graph showing the relationship between alloying time and treatment temperature. The graph and FIG. 4 are schematic diagrams showing an example of a continuous vacuum evaporation plating apparatus. In the drawings: 1 - Steel plate, 2 - Pretreatment furnace, 3a, 3b - Vacuum sealing chamber, 4a, 4b - Vacuum deposition chamber. 5-Cooling chamber Figure 1 1 "Meng (Knob A) f) Feather - Stone G
Fig. 2 (M Chr) Fig. 3 1 2 5 lO2050 treatment
L guard M (hr)
Claims (1)
Si<0.15重量%、Mn:0.15〜0.85重量
%、Ti:0.05〜0.30重量%および不可避的不
純物としてP≦0.020重量%、S≦0.020重量
%、so|A|≦0.050重量%)を蒸着亜鉛メッキ
する際、メッキ直前の鋼板温度を180〜280℃に設
定し、その後、バッチ焼鈍炉内で非酸化性雰囲気で22
0〜320℃、1〜50時間加熱することにより、鉄濃
度が8.0〜12.0重量%の合金化メッキ層を有する
合金化亜鉛メッキ鋼板を製造することを特徴とする方法
。(1) Low carbon titanium killed steel (C≦0.010% by weight,
Si<0.15% by weight, Mn: 0.15-0.85% by weight, Ti: 0.05-0.30% by weight, and unavoidable impurities such as P≦0.020% by weight, S≦0.020% by weight. %, so |
A method of producing an alloyed galvanized steel sheet having an alloyed plated layer with an iron concentration of 8.0 to 12.0% by weight by heating at 0 to 320°C for 1 to 50 hours.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP61272975A JPH07103463B2 (en) | 1986-11-18 | 1986-11-18 | Method for producing alloyed zinc plated steel sheet with excellent deep drawability |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP61272975A JPH07103463B2 (en) | 1986-11-18 | 1986-11-18 | Method for producing alloyed zinc plated steel sheet with excellent deep drawability |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS63128168A true JPS63128168A (en) | 1988-05-31 |
JPH07103463B2 JPH07103463B2 (en) | 1995-11-08 |
Family
ID=17521396
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP61272975A Expired - Lifetime JPH07103463B2 (en) | 1986-11-18 | 1986-11-18 | Method for producing alloyed zinc plated steel sheet with excellent deep drawability |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH07103463B2 (en) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH01283358A (en) * | 1988-02-09 | 1989-11-14 | Nisshin Steel Co Ltd | Production of zinc alloyed galvanized titanium killed steel sheet having superior deep drawability |
JPH05218333A (en) * | 1991-08-31 | 1993-08-27 | Samsung Electron Co Ltd | Semiconductor memory device and its manufacture |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS54110143A (en) * | 1978-02-17 | 1979-08-29 | Mitsubishi Heavy Ind Ltd | Zinc vacuum plating method and equipment |
JPS5983765A (en) * | 1982-11-05 | 1984-05-15 | Nisshin Steel Co Ltd | Manufacture of vacuum deposited galvanized steel sheet efficient in adhesion of plated metal |
-
1986
- 1986-11-18 JP JP61272975A patent/JPH07103463B2/en not_active Expired - Lifetime
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS54110143A (en) * | 1978-02-17 | 1979-08-29 | Mitsubishi Heavy Ind Ltd | Zinc vacuum plating method and equipment |
JPS5983765A (en) * | 1982-11-05 | 1984-05-15 | Nisshin Steel Co Ltd | Manufacture of vacuum deposited galvanized steel sheet efficient in adhesion of plated metal |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH01283358A (en) * | 1988-02-09 | 1989-11-14 | Nisshin Steel Co Ltd | Production of zinc alloyed galvanized titanium killed steel sheet having superior deep drawability |
JPH05218333A (en) * | 1991-08-31 | 1993-08-27 | Samsung Electron Co Ltd | Semiconductor memory device and its manufacture |
Also Published As
Publication number | Publication date |
---|---|
JPH07103463B2 (en) | 1995-11-08 |
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