JPS6140285B2 - - Google Patents
Info
- Publication number
- JPS6140285B2 JPS6140285B2 JP20625283A JP20625283A JPS6140285B2 JP S6140285 B2 JPS6140285 B2 JP S6140285B2 JP 20625283 A JP20625283 A JP 20625283A JP 20625283 A JP20625283 A JP 20625283A JP S6140285 B2 JPS6140285 B2 JP S6140285B2
- Authority
- JP
- Japan
- Prior art keywords
- strength
- steel
- firing
- added
- enameling
- 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.)
- Expired
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Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Description
本発明は、ほうろう性に優れ、かつほうろう焼
成により強度低下が小さい熱延鋼板の製造方法に
関するものである。
従来、ほうろう掛け熱延鋼板の用途は、化学工
業器や温水器等の圧力容器などであり、高い耐食
性とともに鋼板の強度が必要とされるものが主で
ある。高耐食性を得るためには両面ほうろう掛け
をすることが好ましいが、熱延鋼板の場合、冷延
鋼板とは異なり、ほうろう欠陥であるつまとびが
発生し易く、過酷な環境に曝される片面のみにほ
うろう掛けし、他の一面は塗装などで耐食性を保
つ場合が多く、十分な耐食性が得られないという
問題があつた。かかる問題を解決するため、両面
にほうろう掛けできる鋼板が近年開発されてい
る。例えば、特公昭58−1170号、特開昭54−4220
号などに開示されたTi添加鋼がある。これらの
鋼板は、低炭素鋼にTiを添加することにより、
鋼中にTiCを分散せしめ、つまとびの発生を抑制
したものである。
しかし、このうな鋼板は、ほうろう焼成時に
800℃以上に加熱されるため、TiCが粗大化し、
ほうろう焼成後に鋼板の強度が著しく低下すると
いう欠点を有していた。従つて強度が必要とされ
る用途に用いられる場合、予め、非常に高強度の
鋼板を製造し、焼成後の強度を確保することで対
処されてきた。例えば、ほうろう焼成後45Kg／mm2
の強度が要求される場合には、焼成前の強度を60
Kg／mm2とする等の対策がとられてきた。
鋼板を高強度化する方法として、鋼中のＣ量を
多くし、鋼中のTiCの分布を密にして析出強化を
利用する方法、あるいは特開昭54−4220などに示
されるように、Mnなどの固溶強化元素を添加す
る方法がある。前者の方法では焼成による強度低
下が避けられないため、必要な強度を確保するた
めには多量のＣとTiを添加する必要があり、高
コストとなる欠点がある。また、後者の方法によ
れば焼成のよる強度低下は小さいものの、添加す
る元素によつては、ほうろう密着不良やほうろう
泡欠陥などの問題が起り易い。特に、析出硬化を
利用し、焼成前の強度を非常に高くして焼成後に
必要な強度を得ようとした場合、ほうろう処理前
に施されるプレスやロールフオーミング等の加工
が困難になるという欠点も有していた。
本発明は、両面ほうろう掛けTi添加熱延鋼板
の欠点を解消することができるほうろう用熱延鋼
板の製造方法を提供することを目的とする。
本発明は、耐つまとび性に優れ、かつほうろう
焼成後軟化し難い熱延鋼板を製造するに際し、
0.015wt％≦Ｃ≦0.04wt％、0.1wt％≦Ti≦0.25wt
％で、かつ重量％の比でTi／Ｃ≧５、および
0.001wt％≦Ｂ≦0.005wt％を含み、残余が実質的
にFeからなる鋼材を熱間圧延した後、500℃以
上、650℃以下の温度で巻取ることを特徴とする
ほうろう用熱延鋼板の製造方法を提供するもので
ある。
以下に、本発明の内容を詳細に説明する。
Ｃは所定の鋼板強度を得るために含有量を種々
変えることができるが、本発明が対象とする鋼板
の主たる用途である圧力容器等に用いられる場合
の最低強度として一般的な35Kg／mm2以上を得るた
めには、0.015wt％以上必要である。さらに高い
強度が必要な場合、さらにＣ量を増加させること
ができるが、0.04wt％を越えて添加すると、必要
なTi添加量が増大してコスト上昇の原因となる
だけでなく、スリーバー等の鋼板表面欠陥が多く
なるため、上限は0.04wt％とする。
Tiは鋼中でTiC，Ti2S，TiNなどの析出物を形
成し、鋼板の耐つまとび性を向上させる他、TiC
が鋼板の強度を高くする効果をもつ。Ti添加量
が0.1wt％未満であると、つまとび防止の効果は
十分でなく、0.25wt％を越えて添加しても耐つま
とび性の向上はもはや期待できず、また強度への
寄与も小さくなるため、Ti添加量は0.1wt％以上
で0.25wt％以下の範囲にするのが好適である。
Ti／Ｃ、すなわち鋼中のTiとＣとの比は、添
加したTiの耐つまとび性改善および強度上昇の
効果を最大限に発揮させるために重要である。す
なわち、含有量の重量％比でTi／Ｃ＜５の場
合、Tiを0.4wt％以上含有していても、つまとび
抑制の効果は発揮されず、また焼成後の強度低下
が著しくなる。この理由は必ずしも明らかではな
いが、Ti／Ｃ＜５の場合、TiCがほうろう焼成中
に溶解し、焼成後冷却中に再析出する際、粗大化
するためと推定される。
Ｂはほうろう焼成による強度低下を防ぐために
重要な元素である。Ｂを添加しない場合、Tiお
よびＣを適正な範囲で添加したとしても、ほうろ
う焼成による強度低下は避け難い。かかるＢの効
果を発揮せしめるためには0.001wt％以上のＢの
添加が必要である。一方、Ｂ添加量が多くなる
と、連続鋳造時のスラブ表面割れの原因となるた
め、Ｂの添加量は0.005wt％以下とする。
熱延巻取温度も、添加したTiによるつまとび
抑制、強度保持の効果を発揮せしめるために重要
な要因である。すなわち、巻取温度が高すぎると
析出したTiCが粗大化し、つまとび抑制の効果を
十分に発揮しないばかりか、目的とする強度が得
られなくなる。一方、巻取温度が低くすぎると
TiCの析出が不十分で、つまとびの発生が抑制で
きないばかりか、ほうろう焼成による強度低下が
著しくなる。従つて、鋼中のTiに十分につまと
び抑制の効果を発揮せしめるとともに、ほうろう
焼成前後において安定した強度を確保するために
は、500℃以上、650℃以下に温度で巻取ることが
必要である。
以下に本発明を実施例に基き説明する。
〔実施例 １〕
第１表に示す組成を有する鋼塊を溶製し、熱延
終了温度850℃、巻取温度600℃で熱延し、板厚
3.2mmの製品とした。しかる後、塩酸酸洗により
スケールを除去し、下記のようにして、ほうろう
試験および引張試験に供した。これらの試験結果
を第２表に示す。
ほうろう試験は、10％H2 SO4水溶液（75℃）
で５分間酸洗した後、市販のほうろう釉薬を両面
に施釉し、850℃で６分間焼成した。このように
して得られたほうろう掛け板を160℃の恒温槽中
に12時間保持し、冷却後ほうろう表面を観察し、
つまとびの発生および他の表面欠陥の有無を調べ
た。
引張試験は、熱延製品そのまま、およびほうろ
う焼成と同様の熱履歴である860℃、６分、再加
熱後空冷したものとの２種類について、JIS Ｚ
2201による５号試験片を用い、JIS Ｚ 2241にし
たがつて行なつた。
Ti添加量および鋼中TiとＣ量の比が本発明の
範囲内に入つているNo.1〜No.6の鋼は、つまと
び、その他のほうろう表面欠陥は発生しなかつた
が、Ti量が少ないNo.7およびTi／Ｃ＜５である
No.8はつまとびが発生した。また、Ｂを0.001wt
％以上添加したNo.1〜No.4では、ほうろう焼成
前後の鋼板強度の変化は３Kgｆ／mm2以下でほぼ安
定しているが、Ｂを添加していないNo.5，
No.6，No.8では９〜15Kgｆ／mm2強度が低下して
いる。したがつてＢを添加しない場合、ほうろう
焼成後40Kgｆ／mm2の強度を得るためにはNo.8の
如くＣ量を多くし、焼成前強度を55Kgｆ／mm2程度
とする必要があるが、Ｂを添加すれば0.02wt％程
度のＣ量で十分であり、焼成前の強度も40Kgｆ／
mm2程度とすればよいことがわかる。
〔実施例 ２〕
第３表に示す組成の鋼を溶鋼し、熱延終了温度
850℃で熱延し、巻取温度を種々変えて巻取り、
熱延板製品を得た。次いで、塩酸酸洗によりスケ
ールを除去後、実施例１と同じ方法でほうろう試
験および引張試験を行なつた。第４表にその結果
を示す。
第４表からわかるように、巻取温度が480℃の
場合、No.9およびNo.11で、巻取温度が680℃の
場合、No.9，No.10およびNo.11で、つまとびが
発生したが、巻取温度520〜640℃の範囲では、い
ずれの鋼種もつまとびは発生していない。また、
焼成前後の強度変化も、Ｂを0.003wt％添加した
No.9およびNo.10では、巻取温度が520℃以上で
は３Kgｆ／mm2以下で安定している。しかし、Ｂ添
加量が0.001wt％未満のNo.11では、巻取温度が低
い場合には15Kgｆ／mm2以上強度低下があり、巻取
温度が高い場合には焼成前強度が低い。従つて、
ほうろう焼成後の強度は巻取温度によらずほぼ一
定となつている。
以上のように、Ti添加鋼にＢを添加すること
により、耐つまとび性に優れ、かつほうろう焼成
による強度低下の小さいほうろう用熱延鋼板の製
造が可能である。また、巻取温度を変えて異なる
強度の鋼板を製造しても、ほうろう焼成による強
度低下が小さいため、Ti添加量の削減も可能で
あり、また同一組成の鋼を用いて異なる強度のほ
うろう掛け鋼板が製造し得るなど、本発明の工業
的価値は大きい。
The present invention relates to a method for producing a hot-rolled steel sheet that has excellent enameling properties and exhibits little strength loss due to enameling. Conventionally, enameled hot-rolled steel sheets have been mainly used in pressure vessels such as chemical industrial equipment and water heaters, where high corrosion resistance and strength of the steel sheet are required. In order to obtain high corrosion resistance, it is preferable to enamel both sides, but unlike cold-rolled steel sheets, hot-rolled steel sheets are prone to enameling defects, and only one side is exposed to harsh environments. In many cases, corrosion resistance is maintained by enameling one side and painting the other side, which poses the problem that sufficient corrosion resistance cannot be obtained. To solve this problem, steel plates that can be enameled on both sides have been developed in recent years. For example, JP 58-1170, JP 54-4220
There is a Ti-added steel disclosed in No. These steel plates are made by adding Ti to low carbon steel.
TiC is dispersed in the steel to suppress the occurrence of chipping. However, this kind of steel plate cannot be used during enameling firing.
Because it is heated to over 800℃, TiC becomes coarse and
This method had the disadvantage that the strength of the steel sheet decreased significantly after enamel firing. Therefore, when used in applications that require strength, the solution has been to manufacture a very high-strength steel plate in advance and ensure the strength after firing. For example, 45Kg/mm 2 after enameling firing
, the strength before firing should be increased to 60
Countermeasures have been taken, such as setting the limit to Kg/mm 2 . As a method of increasing the strength of steel sheets, there is a method of increasing the amount of C in the steel, densely distributing TiC in the steel, and utilizing precipitation strengthening, or as shown in JP-A-54-4220, etc. There is a method of adding solid solution strengthening elements such as. In the former method, a decrease in strength due to firing is unavoidable, so large amounts of C and Ti must be added to ensure the required strength, resulting in high costs. Furthermore, although the latter method reduces the decrease in strength due to firing, problems such as poor enamel adhesion and enamel bubble defects are likely to occur depending on the added elements. In particular, if precipitation hardening is used to obtain the required strength after firing by increasing the strength before firing, processing such as pressing and roll forming performed before enameling will become difficult. It also had drawbacks. An object of the present invention is to provide a method for manufacturing a hot-rolled steel sheet for enameling, which can eliminate the drawbacks of a hot-rolled steel sheet for enameling on both sides. The present invention provides for the production of hot-rolled steel sheets that have excellent tear resistance and are difficult to soften after enameling.
0.015wt%≦C≦0.04wt%, 0.1wt%≦Ti≦0.25wt
% and in the ratio of weight % Ti/C≧5, and
A hot-rolled steel plate for enameling, characterized by hot rolling a steel material containing 0.001wt%≦B≦0.005wt%, with the remainder substantially consisting of Fe, and then coiling at a temperature of 500°C or higher and 650°C or lower. The present invention provides a method for manufacturing. The contents of the present invention will be explained in detail below. The content of C can be varied in order to obtain a predetermined strength of the steel plate, but the minimum strength of 35 kg/mm 2 is generally used as the minimum strength when used in pressure vessels, etc., which is the main application of the steel plate targeted by the present invention. In order to obtain the above, 0.015wt% or more is required. If even higher strength is required, the amount of C can be further increased, but adding more than 0.04wt% not only increases the amount of Ti required and causes an increase in cost, but also increases the amount of sliver etc. The upper limit is set at 0.04wt% because it increases the number of defects on the surface of the steel sheet. Ti forms precipitates such as TiC, Ti 2 S, and TiN in steel, and improves the chipping resistance of steel sheets.
has the effect of increasing the strength of the steel plate. If the amount of Ti added is less than 0.1wt%, the effect of preventing chipping will not be sufficient, and even if it is added in excess of 0.25wt%, it can no longer be expected to improve the chipping resistance, and it will not contribute to strength. Therefore, the amount of Ti added is preferably in the range of 0.1 wt% or more and 0.25 wt% or less. Ti/C, that is, the ratio of Ti and C in the steel, is important in order to maximize the effect of added Ti on improving chipping resistance and increasing strength. That is, when the weight percent ratio of Ti/C is less than 5, even if Ti is contained at 0.4 wt% or more, the effect of suppressing skipping is not exhibited, and the strength after firing is significantly reduced. The reason for this is not necessarily clear, but it is presumed that when Ti/C<5, TiC dissolves during enamel firing and becomes coarse when reprecipitated during cooling after firing. B is an important element to prevent a decrease in strength due to enamel firing. When B is not added, even if Ti and C are added within appropriate ranges, it is difficult to avoid a decrease in strength due to enamel firing. In order to exhibit the effect of B, it is necessary to add 0.001 wt% or more of B. On the other hand, if the amount of B added increases, it may cause cracks on the surface of the slab during continuous casting, so the amount of B added should be 0.005 wt% or less. The hot-rolling coiling temperature is also an important factor in order for the added Ti to exhibit the effects of suppressing clumping and maintaining strength. In other words, if the winding temperature is too high, the precipitated TiC will become coarse, and not only will the effect of suppressing skipping be insufficient, but also the desired strength will not be obtained. On the other hand, if the winding temperature is too low
TiC precipitation is insufficient, and not only the occurrence of chipping cannot be suppressed, but also the strength decreases significantly due to enamel firing. Therefore, in order to fully exert the effect of suppressing the Ti in the steel and to ensure stable strength before and after enamel firing, it is necessary to coil the steel at a temperature of 500°C or higher and 650°C or lower. be. The present invention will be explained below based on examples. [Example 1] A steel ingot having the composition shown in Table 1 was melted and hot-rolled at a hot-rolling finish temperature of 850°C and a coiling temperature of 600°C.
It was made into a 3.2mm product. Thereafter, scale was removed by pickling with hydrochloric acid, and the samples were subjected to an enameling test and a tensile test as described below. The results of these tests are shown in Table 2. Enamel test uses 10% H2SO4 aqueous solution (75℃)
After pickling for 5 minutes, both sides were glazed with a commercially available enamel glaze and fired at 850°C for 6 minutes. The enameled plate thus obtained was kept in a constant temperature bath at 160°C for 12 hours, and after cooling, the enamel surface was observed.
The presence or absence of skipping and other surface defects was examined. Tensile tests were conducted on two types of hot-rolled products: one as is, and the other after reheating at 860°C for 6 minutes, which has the same thermal history as enamel firing, followed by air cooling.
Testing was carried out in accordance with JIS Z 2241 using a No. 5 test piece according to 2201. Steels No. 1 to No. 6, in which the amount of Ti added and the ratio of Ti to C in the steel were within the range of the present invention, did not have chips or other enamel surface defects, but the amount of Ti No.7 with less and Ti/C<5
In No. 8, a drop occurred. Also, 0.001wt of B
In No. 1 to No. 4, in which B was added at least %, the change in steel sheet strength before and after enameling was almost stable at 3 Kgf/mm 2 or less, but in No. 5, in which B was not added,
In No. 6 and No. 8, the strength decreased by 9 to 15 Kgf/mm 2 . Therefore, if B is not added, in order to obtain a strength of 40 kgf/mm 2 after firing the enamel, it is necessary to increase the amount of C as in No. 8 and make the strength before firing approximately 55 kgf/mm 2 . If B is added, a C amount of about 0.02wt% is sufficient, and the strength before firing is 40Kgf/
It can be seen that a value of about mm 2 is sufficient. [Example 2] Steel having the composition shown in Table 3 was molten, and the hot rolling end temperature was determined.
Hot rolled at 850℃, coiled at various coiling temperatures,
A hot-rolled plate product was obtained. Next, after removing scale by pickling with hydrochloric acid, an enameling test and a tensile test were conducted in the same manner as in Example 1. Table 4 shows the results. As can be seen from Table 4, when the winding temperature is 480°C, No. 9 and No. 11 have no jumps, and when the winding temperature is 680°C, No. 9, No. 10, and No. However, in the coiling temperature range of 520 to 640°C, no skipping occurred in any of the steel types. Also,
The change in strength before and after firing was also determined by adding 0.003wt% B.
In No. 9 and No. 10, the winding temperature was stable at 3 Kgf/mm 2 or less at 520° C. or higher. However, in No. 11 in which the amount of B added was less than 0.001 wt%, the strength decreased by 15 Kgf/mm 2 or more when the winding temperature was low, and the strength before firing was low when the winding temperature was high. Therefore,
The strength after firing the enamel remains almost constant regardless of the winding temperature. As described above, by adding B to Ti-added steel, it is possible to produce a hot-rolled steel sheet for enameling that has excellent chipping resistance and has a small decrease in strength due to enameling firing. In addition, even if steel sheets with different strengths are produced by changing the coiling temperature, the decrease in strength due to enameling is small, so it is possible to reduce the amount of Ti added. The industrial value of the present invention is great because steel plates can be manufactured.
【表】【table】
【表】【table】
【表】【table】
【表】【table】
【表】【table】
Claims (1)
化し難い熱延鋼板を製造するるに際し、0.015wt
％≦Ｃ≦0.04wt％、0.1wt％≦Ti≦0.25wt％で、
かつ重量％の比でTi／Ｃ≧５、および0.001wt％
≦Ｂ≦0.005wt％を含み、残余が実質的にFeから
なる鋼材を熱間圧延した後、500℃以上、650℃以
下の温度で巻取ることを特徴とするほうろう用熱
延鋼板の製造方法。1. When manufacturing hot rolled steel sheets that have excellent chipping resistance and are difficult to soften after enameling, 0.015wt
%≦C≦0.04wt%, 0.1wt%≦Ti≦0.25wt%,
and Ti/C≧5 in weight% ratio, and 0.001wt%
≦B≦0.005wt%, with the remainder being substantially Fe, is hot-rolled and then coiled at a temperature of 500°C or higher and 650°C or lower. .
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20625283A JPS60100622A (en) | 1983-11-02 | 1983-11-02 | Manufacture of hot rolled steel for enamel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20625283A JPS60100622A (en) | 1983-11-02 | 1983-11-02 | Manufacture of hot rolled steel for enamel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS60100622A JPS60100622A (en) | 1985-06-04 |
| JPS6140285B2 true JPS6140285B2 (en) | 1986-09-08 |
Family
ID=16520252
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP20625283A Granted JPS60100622A (en) | 1983-11-02 | 1983-11-02 | Manufacture of hot rolled steel for enamel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS60100622A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS636889U (en) * | 1986-06-28 | 1988-01-18 |
Families Citing this family (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100515021B1 (en) * | 2002-07-02 | 2005-09-15 | 주식회사 포스코 | Ti steel plate manufacturing method for hot mill excellent and steel manufactured by the same method |
| CN100453678C (en) * | 2005-11-16 | 2009-01-21 | 鞍钢股份有限公司 | A hot-rolled double-sided enamel steel plate and its manufacturing method |
| DE102017218434A1 (en) * | 2017-10-16 | 2019-04-18 | Thyssenkrupp Ag | Enameling of high-strength steels |
| CN113373385A (en) * | 2020-02-25 | 2021-09-10 | 宝山钢铁股份有限公司 | Steel for glass lining and manufacturing method thereof |
| CN111411305B (en) * | 2020-04-21 | 2021-09-14 | 五矿营口中板有限责任公司 | High-toughness high-Ti low-alloy steel with thick glass lining and good glass lining performance and manufacturing method thereof |
-
1983
- 1983-11-02 JP JP20625283A patent/JPS60100622A/en active Granted
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS636889U (en) * | 1986-06-28 | 1988-01-18 |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS60100622A (en) | 1985-06-04 |
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