JPH049850B2 - - Google Patents
Info
- Publication number
- JPH049850B2 JPH049850B2 JP8704685A JP8704685A JPH049850B2 JP H049850 B2 JPH049850 B2 JP H049850B2 JP 8704685 A JP8704685 A JP 8704685A JP 8704685 A JP8704685 A JP 8704685A JP H049850 B2 JPH049850 B2 JP H049850B2
- Authority
- JP
- Japan
- Prior art keywords
- steel
- enameling
- adhesion
- enamel
- amount
- 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
Links
- 229910000831 Steel Inorganic materials 0.000 claims description 58
- 239000010959 steel Substances 0.000 claims description 58
- 238000004534 enameling Methods 0.000 claims description 24
- 238000005098 hot rolling Methods 0.000 claims description 18
- 238000005554 pickling Methods 0.000 claims description 16
- 238000000137 annealing Methods 0.000 claims description 9
- 229910052717 sulfur Inorganic materials 0.000 claims description 8
- 238000004519 manufacturing process Methods 0.000 claims description 7
- 229910052698 phosphorus Inorganic materials 0.000 claims description 7
- 238000005097 cold rolling Methods 0.000 claims description 6
- 238000009749 continuous casting Methods 0.000 claims description 6
- 229910052757 nitrogen Inorganic materials 0.000 claims description 5
- 239000012535 impurity Substances 0.000 claims description 2
- 229910052742 iron Inorganic materials 0.000 claims description 2
- 238000001953 recrystallisation Methods 0.000 claims description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims 2
- 210000003298 dental enamel Anatomy 0.000 description 27
- 230000007547 defect Effects 0.000 description 9
- 238000000034 method Methods 0.000 description 9
- 238000010304 firing Methods 0.000 description 8
- 238000005096 rolling process Methods 0.000 description 5
- 239000002344 surface layer Substances 0.000 description 5
- QAOWNCQODCNURD-UHFFFAOYSA-N Sulfuric acid Chemical compound OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 4
- 239000010410 layer Substances 0.000 description 4
- 230000009466 transformation Effects 0.000 description 4
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910000840 Capped steel Inorganic materials 0.000 description 2
- 229910019142 PO4 Inorganic materials 0.000 description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 2
- 241000221561 Ustilaginales Species 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 238000005261 decarburization Methods 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 235000021317 phosphate Nutrition 0.000 description 2
- 150000003013 phosphoric acid derivatives Chemical class 0.000 description 2
- 238000002791 soaking Methods 0.000 description 2
- 150000003467 sulfuric acid derivatives Chemical class 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 238000010998 test method Methods 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 241000080590 Niso Species 0.000 description 1
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000007872 degassing Methods 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000011521 glass Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 239000001257 hydrogen Substances 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 150000004763 sulfides Chemical class 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 238000004804 winding Methods 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Description
<産業上の利用分野>
本発明は、プレス加工後、ほうろう掛して使用
される冷延鋼板の製造方法に関するものである。
<従来技術とその問題点>
ほうろう用鋼板は、泡欠陥や焼成歪の発生を抑
制するために極低炭素鋼であると同時に、表面が
清浄であることが必要である。また、ほうろう焼
成時に鋼板に吸蔵された水素が冷却時に鋼板とほ
うろう層間に浸出してほうろう層をはねとばす現
象であるつまとび欠陥を抑制するため、酸化物、
炭化物、窒化物等の第2相多く鋼中に含有するこ
とが必要である。脱炭脱窒焼鈍したキヤツプド鋼
板は、これらの要求を満たすとともにプレス加工
性も優れており、これまで広くほうろう用鋼板と
して使用されてきた。しかし、脱炭脱窒焼鈍が必
要なため高コストとなることが避けられなかつ
た。
かかる問題を解決するために、特公昭42−
12348号などに開示されているように、プレス成
形性に優れたTi添加極低炭素鋼を用い、脱炭脱
窒焼鈍ではなく連続鋳造法や箱焼鈍法により、ほ
うろう用鋼板を製造する試みが多くなされた。例
えば特開昭51−98619号、特開昭54−125117号な
どに開示されているように、プレス成形性および
耐つまとび性の優れたほうろう用鋼板の製造方法
が種々提案されている。
Ti添加鋼の場合、TiがTiC、TiNあるいはTi
硫化物やTiリン化物を鋼中で形成し、耐つまと
び性を向上せしめると同時に、C、NおよびSが
固溶状態でなくなるため、プレス成形性も良好と
なる。
従つて、つまとびを抑制するためには、十分な
TiとともにC、N、S、Pなどの元素が鋼中に
含有されていることが必要であるとされてきた。
しかし、従来の方法で製造されるほうろう用鋼
板は、ほうろう密着性が脱炭脱窒キヤツプド鋼板
と比べて劣り、またほうろう泡欠陥が発生し易い
などの欠点を有しており問題となつていた。これ
らの欠点をのため、Ti添加極低炭素鋼は特に密
着力の弱い上掛け用ほうろうを直接鋼板に施釉焼
成する直接一回掛ほうろうにはほとんど用いられ
ず、プレス成形性と耐つまとび性を損なうことな
く、表面性状とほうろう密着性を改善する方法が
強く望まれていた。
<発明の目的>
本発明は上述した実状に鑑みてなされたもの
で、プレス成形性と耐つまとび性を損なうことな
く、表面性状とほうろう密着性を優れたものとす
るほうろう用鋼板の製造方法を提供することを目
的とする。
<発明の構成>
以下、本発明を更に詳細に説明する。
本発明者らは、Ti添加鋼をほうろう掛けした
際生じる泡欠陥および密着不良は、ほうろう前処
理として酸洗した特に生成し、表面に付着した
Ti、Fe、S、P、O、Nなどからなるスマツト
が原因であり、このスマツトは熱間圧延時にAr3
変態点以下で圧延し、冷延焼鈍後、表層のみスマ
ツトの付着しにくい集合組織とすることにより抑
制され、かかるスマツト問題に起因する泡欠陥お
よびほうろう密着性が大幅に改善されることを見
い出し、本発明に至つた。
本発明における鋼板の成分の限定理由について
述べる。
用いる鋼板中のC量が多くなるとともに、プレ
ス加工性は劣化し、かつほうろう泡欠陥が発生し
易くなる。本発明で用いる鋼においては、ほうろ
う前処理時のスマツト発生を抑制するため、後述
するように、熱延仕上り温度を低くする必要があ
り、第1図に示すようにC量が0.002wt%をこえ
ると、材質の劣化が著しい。従つてC量は
0.002wt%以下であることが必要である。
ほうろう用鋼板として耐つまとび性を得るため
には、C、N、S、Pを適当量含有することが必
要であるが、同時に良好なプレス成形性を得るた
めにはC量を低くし、かつ後述すうように良好な
ほうろう密着性および良好なほうろう表面を得る
ためには、S、P量をできるだけ低くすることが
必要となる。このため、つまとび抑制のために十
分なN量を添加することが必要となる。
第2図は、N量のみを種々変えた鋼板のつまと
び発生傾向を示すグラフである。C量が0.003wt
%である鋼板を用いてのほうろう掛けの条件は、
つまとびが発生し易くなるように、前処理を20秒
の酸洗のみとし、焼成温度850℃、焼成炉中の露
点を40℃とした。釉薬は市販の日本フエロー製L
タイプ下引釉とし、焼成後160℃に16時間保温し
た後の20枚あたりのつまとびの発生率を示した。
第2図から明らかのごとくC量が低い場合は、N
量が0.009wt%未満ではつまとびが発生し易くな
る。従つてN量は0.009wt%以上であることが必
要である。
Sは鋼中に不可避的不純物として含有される
が、S量が多いとほうろう前処理として通常行わ
れる素地鋼板の酸洗、特に酸洗により生成、鋼板
表面に付着するスマツト量が増加する。スマツト
量が増加すると、ほうろう掛け後、泡欠陥や密着
不良などが起こる。従つて鋼中S量は少ない程ほ
うろう性が向上するが、ほうろう性を改善するた
めには0.008wt%以下とする必要がある。
PはSと同様、ほうろう前処理の酸洗時に多量
のスマツト生成の原因となり、泡欠陥や密着不良
を惹起する。従つてP量もできるだけ少なくする
ことが好ましい。
ほうろう特性の改善の観点からP量は0.01wt%
以下にする必要がある。
Tiは、鋼板のプレス成形性を良好とするとと
もに、鋼中でTiC、TiNおよびTi硫化物、Tiリ
ン化物を形成し、つまとびを防止するために必須
の元素である。かかる2つの目的を達成するため
に、0.05wt%以上添加することが必要である。
しかし、Ti添加量が多くなると、鋼板酸洗時
に生成するスマツト中に含まれるTi量が多くな
り、密着性が劣化する原因となる。Ti含有量の
多いスマツトが特に密着性を劣化せしめる原因は
明確ではないが、通常のスマツトの成分である
Feの酸化物、硫酸塩、リン酸塩のほかに、Ti添
加鋼の場合、Tiを含有する酸化物、硫酸塩、リ
ン酸塩となり、熱的に安定し、ほうろう焼成中に
分解またはほうろう層中に溶解し難くなり、焼成
後、鋼板、ほうろう界面に残存することにより、
密着性が劣化するものと推定される。かかる密着
性の劣化を防止するためには、先に述べたよう
に、S、P量を極力少なくするとともに、Ti量
を0.12wt%以下としなくてはならない。
次に熱延条件について述べる。熱延条件は、本
発明において特に重要である。プレス成形性、ほ
うろう特性を勘案し、上記の如く定められた成分
範囲の鋼は、連続鋳造あるいは造塊一分塊法のい
ずれの方法によつてもスラブとなしうるが、イン
ゴツトの加熱均熱が省略できる連続鋳造法で製造
する方が、コストが安価になり好ましい。
熱間圧延は、プレス成形性の観点からは、Ar3
変態点以上で、終了することが好ましいが、ほう
ろう密着性の観点からはAr3変態点以下、好まし
くはα域で熱間圧延することが必要である。すな
わち、熱間圧延をAr3変態点以上とすると、冷
延、焼鈍後、表面層に{111}集合組織が著しく
発達し、このためほうろう前処理における酸洗時
にスマツトが堆積し易くなり密着性が劣化する。
しかるに熱延仕上り温度をAr3点以下とすると
冷延、焼鈍後の表面層の集合組織は、{111}以外
の集合組織、例えば{110}、{210}、{100}が強
くなり、スマツトの堆積は著しく軽減される。し
かも本発明鋼のごとく成分調整された鋼では鋼板
中心層の集合組織は、熱延仕上り温度の影響が小
さく、Ar3点以下であつても、プレス成形性に好
ましい{111}集合組織が得られる。
従つてほうろう密着性改善の目的からは、熱延
時に表面層の温度がAr3点以下となつてればよい
が、かかる温度域で鋼板の良好な形状が得られ難
い。Ar3点以下で圧延して良好な形状が得られる
のは、820℃以下である。また熱延温度が750℃以
下となると、本発明鋼においても、熱延板で加工
組織が残存し冷延、焼鈍後プレス成形性を得るた
めにはFDTを750℃以上とする必要がある。従つ
て熱間圧延を750℃以上、820℃以下で終了するこ
とがプレス成形性およびほうろう密着性、双方を
満足させるためには必要である。
熱延後の巻取、デスケーリング、冷間圧延、再
結晶焼鈍は、従来より一般的に行われているいか
なる方法を採用しても、本発明の目的とするとこ
ろは達成し得る。
<実施例>
本発明を実施例に基き具体的に説明する。
表1に示す組成の鋼を転炉およびRH脱ガス工
程により溶製し、連続鋳造法によりスラブとし
た。
表1に示したNo.1〜9の鋼を熱延後、冷延で板
厚0.7mmとし、800℃、30秒間の均熱時間をとつて
連続焼鈍した。次いで0.8%の調負圧延を施した。
鋼中のC量と延性の関係を第1図に示す。引つ張
り試験は、JIS5号引つ張り試験片で行つた。C量
が増加すると延性は劣化する。50%以上の延性を
確保するためには、C量を0.002wt%以下とする
必要がある。
本発明鋼の特徴であるほうろう前処理(硫酸酸
洗)時のスマツト生成が熱延仕上り温度にいかに
影響されるかを示したのが第3図である。表1の
No.3、No.5の2種類の鋼で各々熱延仕上り温度を
820℃以上で終了した場合(a)と780℃以上820℃以
下で終了した場合(b)とに分けた。(a)と(b)では、酸
洗されていく間に、スマツト量に大きな差が出て
くる。このことは、表面の集合組織ともよく対応
する。
表2は集合組織の測定結果であるが、スマツト
量の多い鋼は{222}面の強度は強くなり、逆に
スマツトのあまり発生していない鋼は{222}面
の強度は弱くなり、逆に{220}面および{211}
面の強度が強くなつており、仕上り圧延温度とよ
く対応する。
上記のそれぞれの鋼板のほうろう密着性を調べ
るためには、前処理として硫酸酸洗(10%
H2SO4、75℃)、Ni浴浸漬(2%NiSO4、65℃)
の時間を種々変えて処理した鋼板に市販の上掛け
釉〔日本フエロー製1553B(Ti白釉)〕を施釉し、
820℃で焼成後、P.E.I(米国ほうろう協会)が推
奨する密着試験方法(ASTM;C313−59)によ
り密着性を測定した。この試験方法では、ほうろ
う掛け鋼板を変形させ、変形部においてほうろう
が剥離しなかつた部分の面積率を測定するもの
で、密着指数100%のものが良好、0%のものが
不良である。
第4図は、スマツト発生量の多い鋼板(No.3−
a)と少ない鋼板(No.3−b)の種々の酸洗減量
におけるほうろう密着性を示したものである。比
較例のNo.3−aではスマツトがまだそれほど発生
していないある一点の酸洗減量時の密着指数が80
%越えているほかは、安定した密着性は得られな
い。また、その表面はピンホールが目立ちその他
の酸洗減量域ではピンホールとともに肌荒れも見
られた。それに比べスマツト発生量の少ない本発
明例No.3−bの鋼板は広い酸洗減量域で良好な密
着性が安定して得られ、表面性状も良好となつ
た。
<Industrial Application Field> The present invention relates to a method for manufacturing a cold rolled steel sheet which is used by enameling after pressing. <Prior art and its problems> Steel plates for enameling need to be ultra-low carbon steel and have a clean surface in order to suppress the occurrence of bubble defects and firing distortion. In addition, in order to suppress the skipping defect, which is a phenomenon in which hydrogen stored in the steel sheet during enamel firing leaks between the steel sheet and the enamel layer during cooling and causes the enamel layer to fly away, oxides,
It is necessary to contain a large amount of second phase such as carbides and nitrides in the steel. Decarburized and denitrified annealed capped steel sheets satisfy these requirements and have excellent press workability, and have been widely used as steel sheets for enameling. However, since decarburization and denitrification annealing is required, high costs are unavoidable. In order to solve this problem,
As disclosed in No. 12348 and other publications, attempts have been made to manufacture steel sheets for enameling using Ti-added ultra-low carbon steel with excellent press formability and using continuous casting or box annealing instead of decarburization and denitrification annealing. A lot was done. For example, as disclosed in JP-A-51-98619 and JP-A-54-125117, various methods for producing enameled steel sheets with excellent press formability and resistance to chipping have been proposed. In the case of Ti-added steel, Ti is TiC, TiN or Ti
Sulfides and Ti phosphides are formed in the steel to improve flaking resistance, and at the same time, since C, N, and S are no longer in a solid solution state, press formability is also improved. Therefore, in order to suppress tripping, sufficient
It has been considered necessary for steel to contain elements such as C, N, S, and P along with Ti. However, steel sheets for enameling manufactured by conventional methods have problems such as inferior enamel adhesion compared to decarburized and denitrified capped steel sheets, and the tendency to generate enamel bubble defects. . Because of these drawbacks, Ti-added ultra-low carbon steel is rarely used for direct single-ply enamel, in which over-ply enamel, which has weak adhesion, is directly glazed and fired onto a steel plate, and has poor press formability and flaking resistance. There has been a strong desire for a method to improve the surface texture and enamel adhesion without impairing the enamel. <Object of the invention> The present invention has been made in view of the above-mentioned actual situation, and provides a method for producing a steel plate for enameling that has excellent surface properties and enamel adhesion without impairing press formability and chipping resistance. The purpose is to provide <Structure of the Invention> The present invention will be described in more detail below. The present inventors found that the bubble defects and poor adhesion that occur when Ti-added steel is enameled are caused by pickling as a pre-enameling treatment.
The cause is smut made of Ti, Fe, S, P, O, N, etc., and this smut is formed by Ar 3 during hot rolling.
We have discovered that by rolling below the transformation point and creating a texture that makes it difficult for smut to adhere only to the surface layer after cold rolling annealing, the bubble defects and enamel adhesion caused by the smut problem can be suppressed, and the enamel adhesion and bubble defects caused by the smut problem can be greatly improved. This led to the present invention. The reasons for limiting the components of the steel plate in the present invention will be described. As the amount of C in the steel plate used increases, press workability deteriorates and enamel bubble defects are more likely to occur. In the steel used in the present invention, in order to suppress the occurrence of smut during pre-enameling treatment, it is necessary to lower the hot-rolling finishing temperature as described later, and as shown in Figure 1, the C content is 0.002wt%. If it exceeds this, the material will deteriorate significantly. Therefore, the amount of C is
It needs to be 0.002wt% or less. In order to obtain chipping resistance as a steel plate for enameling, it is necessary to contain appropriate amounts of C, N, S, and P, but at the same time, in order to obtain good press formability, the amount of C should be lowered, In addition, as will be described later, in order to obtain good enamel adhesion and a good enamel surface, it is necessary to reduce the amounts of S and P as much as possible. Therefore, it is necessary to add a sufficient amount of N to suppress the skipping. FIG. 2 is a graph showing the tendency of jumps in steel sheets in which only the amount of N was varied. C amount is 0.003wt
The conditions for enameling using a steel plate with a
In order to facilitate the occurrence of skipping, the pretreatment was only pickling for 20 seconds, the firing temperature was 850°C, and the dew point in the firing furnace was 40°C. The glaze is commercially available Nippon Fellow L.
The rate of occurrence of flaking per 20 pieces after firing and keeping at 160°C for 16 hours is shown.
As is clear from Figure 2, when the amount of C is low, N
If the amount is less than 0.009wt%, skipping tends to occur. Therefore, the amount of N needs to be 0.009wt% or more. S is contained in steel as an unavoidable impurity, but when the amount of S is large, the amount of smut produced and attached to the surface of the steel sheet increases during pickling of the base steel sheet, which is usually performed as a pre-enameling treatment, especially during pickling. If the amount of smut increases, bubble defects and poor adhesion will occur after enameling. Therefore, the smaller the amount of S in the steel, the better the enameling properties, but in order to improve the enameling properties, it is necessary to keep it at 0.008wt% or less. Like S, P causes the formation of a large amount of smut during pickling in pre-enamel treatment, causing bubble defects and poor adhesion. Therefore, it is preferable to reduce the amount of P as much as possible. From the perspective of improving enamel properties, the amount of P is 0.01wt%.
It is necessary to do the following. Ti is an essential element for improving the press formability of a steel sheet, forming TiC, TiN, Ti sulfide, and Ti phosphide in the steel, and preventing flaking. In order to achieve these two objectives, it is necessary to add 0.05 wt% or more. However, when the amount of Ti added increases, the amount of Ti contained in the smut generated during pickling of the steel sheet increases, causing deterioration of adhesion. It is not clear why Smuts with a high Ti content cause particularly poor adhesion, but it is a component of normal Smuts.
In addition to Fe oxides, sulfates, and phosphates, in the case of Ti-added steels, Ti-containing oxides, sulfates, and phosphates become thermally stable and decompose during enamel firing or enamel layer. After firing, it becomes difficult to dissolve in the steel plate and remains at the interface between the steel plate and the enamel.
It is estimated that the adhesion will deteriorate. In order to prevent such deterioration of adhesion, as mentioned above, the amounts of S and P must be reduced as much as possible, and the amount of Ti must be kept at 0.12 wt% or less. Next, the hot rolling conditions will be described. Hot rolling conditions are particularly important in the present invention. Taking press formability and enameling properties into consideration, steel with the composition range determined above can be made into a slab by either continuous casting or the one-time ingot method, but heating and soaking of the ingot It is preferable to manufacture by a continuous casting method which can omit the process because the cost is low. From the viewpoint of press formability, hot rolling is Ar 3
Although it is preferable to complete hot rolling at a temperature above the transformation point, from the viewpoint of enameling adhesion, it is necessary to hot-roll below the Ar 3 transformation point, preferably in the α region. In other words, when hot rolling is carried out above the Ar 3 transformation point, {111} texture develops significantly in the surface layer after cold rolling and annealing, which makes it easier for smut to accumulate during pickling in pre-enameling treatment, resulting in poor adhesion. deteriorates. However, when the hot rolling finishing temperature is set to 3 Ar points or less, the texture of the surface layer after cold rolling and annealing becomes stronger with textures other than {111}, such as {110}, {210}, and {100}, resulting in a smooth surface layer. deposition is significantly reduced. Moreover, in steels with controlled compositions such as the steel of the present invention, the texture of the center layer of the steel sheet is less affected by the hot-rolling finishing temperature, and even if the Ar is 3 points or less, a {111} texture favorable for press formability can be obtained. It will be done. Therefore, for the purpose of improving enamel adhesion, it is sufficient that the temperature of the surface layer during hot rolling is below Ar 3 points, but it is difficult to obtain a good shape of the steel sheet in such a temperature range. A good shape can be obtained by rolling at 3 Ar points or less at 820°C or less. Further, when the hot rolling temperature is 750°C or lower, even in the steel of the present invention, the processed structure remains in the hot rolled sheet, and in order to obtain press formability after cold rolling and annealing, the FDT needs to be 750°C or higher. Therefore, in order to satisfy both press formability and enamel adhesion, it is necessary to complete the hot rolling at a temperature of 750°C or higher and 820°C or lower. The purpose of the present invention can be achieved by any conventionally conventional method for winding, descaling, cold rolling, and recrystallization annealing after hot rolling. <Example> The present invention will be specifically explained based on an example. Steel having the composition shown in Table 1 was melted using a converter and an RH degassing process, and was made into a slab using a continuous casting method. Steels Nos. 1 to 9 shown in Table 1 were hot-rolled, then cold-rolled to a thickness of 0.7 mm, and continuously annealed at 800° C. with a soaking time of 30 seconds. Next, 0.8% negative rolling was performed.
Figure 1 shows the relationship between the amount of C in steel and ductility. The tensile test was conducted using a JIS No. 5 tensile test piece. As the amount of C increases, ductility deteriorates. In order to ensure ductility of 50% or more, the amount of C needs to be 0.002wt% or less. FIG. 3 shows how smut formation during enameling pretreatment (sulfuric acid pickling), which is a feature of the steel of the present invention, is influenced by hot rolling finishing temperature. Table 1
Two types of steel, No. 3 and No. 5, have different hot rolling finishing temperatures.
It was divided into cases where the test ended at 820°C or higher (a) and cases where the test ended at 780°C or higher and 820°C or lower (b). Between (a) and (b), there is a large difference in the amount of smut during pickling. This corresponds well to the texture of the surface. Table 2 shows the results of texture measurements. Steel with a large amount of smut has a strong {222} plane, while steel with little smut has a weak {222} plane, and vice versa. {220} plane and {211}
The surface strength is strong and corresponds well to the finish rolling temperature. In order to examine the enamel adhesion of each of the above steel sheets, sulfuric acid pickling (10%
H 2 SO 4 , 75°C), Ni bath immersion (2% NiSO 4 , 65°C)
A commercially available top glaze [1553B (Ti white glaze) manufactured by Nippon Ferro] is applied to the steel plate treated for various times.
After firing at 820°C, adhesion was measured using the adhesion test method (ASTM; C313-59) recommended by PEI (American Enamel Institute). In this test method, an enameled steel plate is deformed and the area ratio of the deformed part where the enamel has not peeled off is measured. An adhesion index of 100% is considered good, and an adhesion index of 0% is considered bad. Figure 4 shows a steel plate with a large amount of smut (No. 3-
This figure shows the enamel adhesion of a) and a small steel plate (No. 3-b) at various pickling losses. In Comparative Example No. 3-a, the adhesion index at the time of pickling loss at one point where smut has not yet occurred is 80.
%, stable adhesion cannot be obtained. In addition, pinholes were noticeable on the surface, and in other pickling loss areas, pinholes and rough skin were also observed. In comparison, the steel plate of Example No. 3-b of the present invention, which had a smaller amount of smut, stably obtained good adhesion over a wide pickling loss range and had good surface quality.
【表】【table】
【表】
<発明の効果>
上述のように、ほうろう用鋼板として必要なプ
レス成形性、耐つまとび性、ほうろう密着性、表
面性状の諸特性を全て満たす鋼板を製造すること
は、本発明で明らかにされたごとく、鋼中の諸成
分量を厳密に調整し、かつ熱延時のスラブの仕上
り圧延温度を適切に制御することにより、、はじ
めて可能となるものである。
本発明により、従来造塊法で製造されていた高
級ほうろう用鋼板が連鋳法により製造し得ること
になり、コストおよび省エネルギーの点からも非
常に大きなメリツトがもたらされる。[Table] <Effects of the Invention> As mentioned above, the present invention makes it possible to manufacture a steel plate that satisfies all the properties necessary for a steel plate for enameling, such as press formability, chipping resistance, enameling adhesion, and surface texture. As has been made clear, this can only be achieved by strictly adjusting the amounts of various components in the steel and appropriately controlling the finish rolling temperature of the slab during hot rolling. According to the present invention, high-grade enameling steel sheets, which were conventionally manufactured by the ingot method, can be manufactured by the continuous casting method, which brings about great advantages in terms of cost and energy saving.
第1図は、鋼中C量と延性の関係を示すグラフ
である。第2図は、つまとび抑制に必要な鋼中N
量を示すグラフである。第3図および第4図は、
それぞれ酸洗時間がスマツト量におよぼす仕上り
温度の影響およびほうろう密着性におよぼす仕上
り温度の影響を示すグラスである。
FIG. 1 is a graph showing the relationship between C content in steel and ductility. Figure 2 shows the N in steel required to suppress tripping.
It is a graph showing the amount. Figures 3 and 4 are
These glasses show the effect of finishing temperature on pickling time on smut amount and the effect of finishing temperature on enamel adhesion, respectively.
Claims (1)
性に優れたほうろう用鋼板を製造するに際し、C
≦0.002wt%、0.009wt%≦N、S≦0.008wt%、
P≦0.01wt%、0.05wt%≦Ti≦0.12、残部鉄およ
び不可避的不純物よりなる鋼を連続鋳造してスラ
ブとなした後、熱延仕上り温度を750℃から820℃
の範囲で熱間圧延し、次いで酸洗、冷延、再結晶
焼鈍を施すことを特徴とするほうろう用鋼板の製
造方法。1. When manufacturing a steel plate for enameling with excellent press formability, enameling adhesion, and chipping resistance, C
≦0.002wt%, 0.009wt%≦N, S≦0.008wt%,
After continuous casting of steel consisting of P≦0.01wt%, 0.05wt%≦Ti≦0.12, balance iron and unavoidable impurities to form a slab, the hot rolling finishing temperature is changed from 750℃ to 820℃.
1. A method for producing a steel plate for enameling, which comprises hot rolling in a range of 100 to 100 ml, followed by pickling, cold rolling, and recrystallization annealing.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP8704685A JPS61246325A (en) | 1985-04-23 | 1985-04-23 | Manufacture of steel sheet for enameling |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP8704685A JPS61246325A (en) | 1985-04-23 | 1985-04-23 | Manufacture of steel sheet for enameling |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS61246325A JPS61246325A (en) | 1986-11-01 |
JPH049850B2 true JPH049850B2 (en) | 1992-02-21 |
Family
ID=13903995
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP8704685A Granted JPS61246325A (en) | 1985-04-23 | 1985-04-23 | Manufacture of steel sheet for enameling |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS61246325A (en) |
Families Citing this family (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0653914B2 (en) * | 1987-07-20 | 1994-07-20 | 住友金属工業株式会社 | Steel plate for enamel and its manufacturing method |
KR20040017758A (en) * | 2002-08-23 | 2004-02-27 | 주식회사 포스코 | Hot strip manufacturing method in mini-mill process by using nitrogen |
-
1985
- 1985-04-23 JP JP8704685A patent/JPS61246325A/en active Granted
Also Published As
Publication number | Publication date |
---|---|
JPS61246325A (en) | 1986-11-01 |
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