JPH0639679B2 - Steel sheet with galvannealed alloy - Google Patents
Steel sheet with galvannealed alloyInfo
- Publication number
- JPH0639679B2 JPH0639679B2 JP61208800A JP20880086A JPH0639679B2 JP H0639679 B2 JPH0639679 B2 JP H0639679B2 JP 61208800 A JP61208800 A JP 61208800A JP 20880086 A JP20880086 A JP 20880086A JP H0639679 B2 JPH0639679 B2 JP H0639679B2
- Authority
- JP
- Japan
- Prior art keywords
- content
- steel sheet
- alloyed
- plating layer
- layer
- 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 - Fee Related
Links
- 229910000831 Steel Inorganic materials 0.000 title claims description 11
- 239000010959 steel Substances 0.000 title claims description 11
- 229910045601 alloy Inorganic materials 0.000 title description 3
- 239000000956 alloy Substances 0.000 title description 3
- 238000007747 plating Methods 0.000 claims description 30
- 229910001335 Galvanized steel Inorganic materials 0.000 claims description 7
- 239000008397 galvanized steel Substances 0.000 claims description 7
- 229910052745 lead Inorganic materials 0.000 claims description 7
- 239000012535 impurity Substances 0.000 claims description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 26
- 238000000227 grinding Methods 0.000 description 22
- 229910052742 iron Inorganic materials 0.000 description 12
- 230000000694 effects Effects 0.000 description 8
- 238000005275 alloying Methods 0.000 description 7
- 239000011248 coating agent Substances 0.000 description 6
- 238000000576 coating method Methods 0.000 description 6
- 239000000463 material Substances 0.000 description 4
- 238000005246 galvanizing Methods 0.000 description 3
- 230000003247 decreasing effect Effects 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 238000011282 treatment Methods 0.000 description 2
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- 229910001297 Zn alloy Inorganic materials 0.000 description 1
- 229910007570 Zn-Al Inorganic materials 0.000 description 1
- 230000001154 acute effect Effects 0.000 description 1
- 238000013459 approach Methods 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000008021 deposition Effects 0.000 description 1
- 238000003618 dip coating Methods 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- KFZAUHNPPZCSCR-UHFFFAOYSA-N iron zinc Chemical compound [Fe].[Zn] KFZAUHNPPZCSCR-UHFFFAOYSA-N 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000000843 powder Substances 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
Landscapes
- Coating With Molten Metal (AREA)
Description
【発明の詳細な説明】 ［産業上の利用分野］ 本発明は合金化溶融亜鉛めっき鋼板に関し、さらに詳し
くは、加工性に優れた合金化溶融亜鉛めっき鋼板に関す
る。TECHNICAL FIELD The present invention relates to an alloyed hot-dip galvanized steel sheet, and more particularly to an alloyed hot-dip galvanized steel sheet having excellent workability.
［従来技術］ 鋼板(鋼帯)に溶融亜鉛めっきを施した後、板温４５０〜
６００℃となるように加熱処理することによって、亜鉛
めっき層が亜鉛−鉄合金めっき層になった、所謂、合金
化溶融亜鉛めっき鋼板は、その優れた塗装性、溶接性の
ため自動車、家庭電器などの用途に使用され、その生産
量は増加の傾向にある。[Prior Art] After hot-dip galvanizing a steel plate (steel strip), the plate temperature is 450 to
The so-called alloyed hot-dip galvanized steel sheet, in which the galvanized layer becomes a zinc-iron alloy plated layer by heat treatment at 600 ° C., has excellent paintability and weldability. It is used for such purposes, and its production tends to increase.
しかしながら、この合金化溶融亜鉛めっき層は、Ｆeと
Ｚnの金属間化合物であるため硬くて脆いという弱点が
ある。それ故、強い加工、例えば、自動車車体のフエン
ダの形にプレス加工が施された場合に、めっき層がパウ
ダリング、または、剥離することによってプレス型など
に付着し、これが堆積してプレス製品に転写する、所
謂、星目などのトラブルを生じるなど加工性に問題があ
る。However, this alloyed hot-dip galvanized layer has a weak point that it is hard and brittle because it is an intermetallic compound of Fe and Zn. Therefore, when strong processing, for example, press processing is applied to the shape of a car body's fender, the plating layer adheres to the press mold by powdering or peeling, and this deposits on the press product. There is a problem in workability such as transfer, so-called trouble such as star eyes, etc.
そのため、合金化溶融亜鉛めっき層のＺnとＦｅの合金
化の程度、即ち、合金化めっき層中の鉄含有量を 8〜13
wt％の範囲とすべく合金化加熱温度、時間等の条件を厳
密に制御する必要があり、品質の安定性、歩留り等が低
下する問題がある。なお、鉄含有量が 8wt％未満ではめ
っき層の表面まで合金層が発達せず、また、13wt％を越
えると合金化めっき層の硬度が高くなって加工性が劣化
する。Therefore, the degree of alloying of Zn and Fe in the galvannealed layer, that is, the iron content in the galvannealed layer is 8 to 13
It is necessary to strictly control the conditions such as the alloying heating temperature and the time so as to be in the range of wt%, and there is a problem that the quality stability, the yield, etc. are reduced. If the iron content is less than 8 wt%, the alloy layer does not develop to the surface of the plated layer, and if it exceeds 13 wt%, the hardness of the alloyed plated layer increases and the workability deteriorates.
その他、合金化めっき層の付着量は加工性の面から片面
当たり７０〜９０g/m2に制限せざるを得なくなり、厚め
っきが必要な腐蝕環境の厳しい用途への適用が自ずと抑
えられているのが現状である。In addition, from the viewpoint of workability, the deposition amount of the alloyed plating layer has to be limited to 70 to 90 g / m 2 per side, which naturally limits its application to severe corrosion environments requiring thick plating. is the current situation.
［発明が解決しようとする問題点］ 本発明は上記に説明したような従来における合金化めっ
き層の種々の問題点に鑑み、本発明者が鋭意研究を行っ
た結果、合金化めっき層の加工性を改善するためにＴ
i、Ａl、Ｐbを含有させることによって、加工性が著し
く向上することを見出し、合金化溶融亜鉛めっき鋼板を
開発したのである。[Problems to be Solved by the Invention] In view of various problems of the conventional alloyed plating layer as described above, the present invention has been earnestly studied by the present inventor, and as a result, processing of the alloyed plating layer was performed. T to improve sex
It was found that the workability was remarkably improved by containing i, Al, and Pb, and a galvannealed steel sheet was developed.
［問題点を解決するための手段］ 本発明に係る合金化溶融亜鉛めっき鋼板は、 (１)Ａｌ0.05〜70wt％、Ｔｉ0.0002〜0.5wt％を含有
し、残部Ｚnおよび不可避不純物よりなる合金化めっき
層を有することを特徴とする合金化溶融亜鉛めっき鋼板
を第１の発明とし、 (２)Ａｌ0.05〜70wt％、Ｔｉ0.0002〜0.5wt％、Ｐｂ1.0
wt％以下 を含有し、残部Ｚnおよび不可避不純物よりなる合金化
めっき層を有することを特徴とする合金化溶融亜鉛めっ
き鋼板を第２の発明とする２つの発明よりなるものであ
る。[Means for Solving the Problems] The galvannealed steel sheet according to the present invention contains (1) Al 0.05 to 70 wt% and Ti 0.0002 to 0.5 wt%, and the balance Zn and unavoidable impurities. A first invention is an alloyed hot-dip galvanized steel sheet having an alloyed plating layer. (2) Al0.05-70wt%, Ti0.0002-0.5wt%, Pb1.0
A second aspect of the present invention is an alloyed hot-dip galvanized steel sheet characterized by having an alloyed plating layer containing less than wt% and the balance being Zn and unavoidable impurities.
本発明に係る合金化溶融亜鉛めっき鋼板について以下詳
細に説明する。The galvannealed steel sheet according to the present invention will be described in detail below.
先ず、本発明に係る合金化溶融亜鉛めっき鋼板の合金化
めっき層中の含有成分および含有割合について説明す
る。First, the content components and content ratios in the alloy-plated layer of the galvannealed steel sheet according to the present invention will be described.
Ｔi含有量について説明すると、第１図はＴi含有量と合
金化めっき層の耐パウダリング性の関係を示したもので
ある(片面当たりの付着量５０g/m2。)。なお、耐パウダ
リング性の評価は合金化溶融亜鉛めっき鋼板を６０゜の
鋭角に曲げ、内面側に合金化めっき層の亀裂およびパウ
ダリング状剥離の程度を肉眼観察し、第１表に示す評価
基準に従って行う。Explaining the Ti content, FIG. 1 shows the relationship between the Ti content and the powdering resistance of the alloyed plating layer (adhesion amount per one side: 50 g / m 2 ). The powdering resistance was evaluated by bending the alloyed hot-dip galvanized steel sheet at an acute angle of 60 ° and visually observing the degree of cracking and powdery peeling of the alloyed plating layer on the inner surface side. Follow the standards.
最初に合金化めっき層中鉄含有量が11wt％の場合につい
て説明する。 First, the case where the iron content in the alloyed plating layer is 11 wt% will be described.
この場合Ｔi含有量が 0wt％の場合合金化めっき層はパ
ウダリングは起こさないが、亀裂が発生する。これに対
し、Ｔi含有量が 0.0001wt％においては変化が認められ
ないが、Ｔi含有量が0.0002wt％になると亀裂は認めら
れなくなり、さらに、Ｔi含有量が増加しても亀裂は認
められない。また、鉄含有量が15wt％の場合、Ｔi含有
量が 0wt％で合金化めっき層はかなりのパウダリング現
象が発生する。これに対しＴi含有量が0.0001wt％でパ
ウダリングはわずかな程度にまで抑制され、さらに、Ｔ
i含有量が 0.0002wt％になるとパウダリングは全く認め
られなくなり、Ｔi 含有量がそれ以上に増加しても良好
な耐パウダリング性が維持される。第１図で○は鉄含有
量 11wt％を示し、×は鉄含有量 15wt％を示す。In this case, when the Ti content is 0 wt%, the alloyed plating layer does not powder, but cracks. On the other hand, no change was observed at a Ti content of 0.0001 wt%, but no cracks were observed at a Ti content of 0.0002 wt%, and no cracks were observed even if the Ti content was increased. . Further, when the iron content is 15 wt%, the Ti content is 0 wt%, and a considerable powdering phenomenon occurs in the alloyed plating layer. On the other hand, when the Ti content is 0.0001 wt%, powdering is suppressed to a slight extent.
When the i content is 0.0002 wt%, no powdering is observed, and even if the Ti content is further increased, good powdering resistance is maintained. In FIG. 1, ◯ indicates an iron content of 11 wt% and x indicates an iron content of 15 wt%.
この結果から、合金化めっき層中のＴi含有量の下限
は、パウダリング性の向上が顕著に認められる 0.0002w
t％とし、上限については 0.5wt％を越えて含有される
と効果が飽和すると共に経済的でない。よって、Ｔi含
有量は 0.0002〜0.5wt ％とする。From these results, the lower limit of the Ti content in the alloyed plating layer is remarkably improved in powdering property.
The upper limit is t%, and if the upper limit is more than 0.5 wt%, the effect is saturated and it is not economical. Therefore, the Ti content is 0.0002 to 0.5 wt%.
このように合金化めっき層にＴiを含有させることによ
って耐パウダリング性が向上するのは、Ｆe−Ｚn合金層
にＴiが含有されると変形能が向上するものと考えられ
る。The reason why the powdering resistance is improved by including Ti in the alloyed plating layer is considered to be that the deformability is improved when Ti is contained in the Fe-Zn alloy layer.
本発明に係る合金化溶融亜鉛めっき鋼板においては、合
金化めっき層中にＴiの他にＡlおよびＰbを含有する。In the galvannealed steel sheet according to the present invention, Al and Pb are contained in the alloyed plating layer in addition to Ti.
Ａlは溶融亜鉛めっきでは浴中Ａl含有量は通常0.1〜0.3
wt％であるため、めっき層中では同一レベルあるいは濃
縮されて 0.1〜1wt％となるが、浴中にＡlを 1〜60wt％
を含有するＺn−Ａl系合金めっきにおけるめっき層中Ａ
l含有量は 1〜70wt％となり、この含有量でも効果があ
る。Al is usually 0.1 to 0.3 in the bath in hot dip galvanizing.
Since it is wt%, it is 0.1 to 1 wt% at the same level or concentrated in the plating layer, but Al is 1 to 60 wt% in the bath.
A in the plating layer in Zn-Al alloy plating containing
The l content is 1 to 70 wt%, and this content is effective.
Ｐbは非合金化材の１種であるレジュラースパングル材
を合金化材と同一めっき浴で製造する場合には、スパン
グル成長のためＰbをめっき浴中に最大約 1.0wt％含有
させるため、めっき層にも同一レベルのＰb含有量約 1.
0wt％含有される。また、レギュラースパングル材を同
一浴で製造しない場合には、Ｐbを浴に含有させる必要
がないのでめっき層中のＰb含有量は 0wt％となる。よ
って、Ｐb含有量は 1.0wt％以下とする。Pb is a type of non-alloyed material. When a regular spangle material is manufactured in the same plating bath as the alloyed material, Pb is included in the plating bath at a maximum of about 1.0 wt% for spangle growth. The same level of Pb content in the layers is about 1.
Contains 0 wt%. Further, when the regular spangle material is not manufactured in the same bath, it is not necessary to add Pb to the bath, so the Pb content in the plating layer is 0 wt%. Therefore, the Pb content should be 1.0 wt% or less.
また、上記したＴi、Ａl、Ｐbの含有成分以外にＦeが通
常の合金化程度では含有量は 7〜15wt％であるが、さら
に、高合金化になって合金化めっき層がΓ相(Ｆe3Ｚ
n10)に近づきＦe含有量が15〜30wt％に増加することも
ある。In addition to the above-mentioned Ti, Al, and Pb content components, the content of Fe is 7 to 15 wt% in a normal alloying degree. 3 Z
The Fe content may increase to 15 to 30 wt% as it approaches n 10 ).
［実施例］ 本発明に係る合金化溶融亜鉛めっき鋼板の実施例を説明
する。[Example] An example of the galvannealed steel sheet according to the present invention will be described.
実施例 １ 溶融めっきラインを用いて、めっき浴中のＡｌ含有量を
0.12wt％とし、Ｐb含有量 0.2wt％、Ｔiを 0.0050wt％
含有した場合と、含有しない場合について、溶融亜鉛め
っきおよび合金化処理を実施した。Example 1 Using a hot dip coating line, the Al content in the plating bath was measured.
0.12wt%, Pb content 0.2wt%, Ti 0.0050wt%
Hot-dip galvanizing and alloying treatment were carried out with and without containing.
なお、耐パウダリング性に及ぼすめっき付着量および合
金化めっき層中のＦe含有量の影響を明らかにするため
に、ワイピング条件および合金化条件を種々に変えた。The wiping conditions and the alloying conditions were variously changed in order to clarify the effects of the coating amount and the Fe content in the alloyed plating layer on the powdering resistance.
また、得られた合金化めっき層中のＴi含有量は 0.0070
wt％であり、Ａl含有量は 0.21wt％、Ｐb含有量は 0.19
wt％であった(Ａl、Ｐb含有量はＴiの含有の有り、なし
に関係なく同一である。)。Also, the Ti content in the obtained alloyed plating layer is 0.0070.
wt%, Al content is 0.21 wt%, Pb content is 0.19
wt% (Al and Pb contents are the same regardless of whether Ti is contained or not).
第２図はめっき付着量と耐パウダリング性の関係に及ぼ
すＴi含有の影響を示し(Ｆe含有量は11wt％)、Ｔiを含
有しない場合、めっき付着量の増加と共に耐パウダリン
グ性は急激に劣化するが、Ｔiを含有する場合はめっき
付着量の増加と共に耐パウダリング性は若干低下するに
留どまり、めっき付着量１１０g/m2で亀裂が発生するの
みで実用上殆ど問題はなく、使用範囲の拡大が可能であ
る。この第２図において、×はＴi含有量 0.0070wt％、
○はＴi含有量が 0wt％を示す。Fig. 2 shows the effect of Ti content on the relationship between the coating weight and the powdering resistance (Fe content is 11 wt%). If Ti is not contained, the powdering resistance rapidly increases as the coating weight increases. Although it deteriorates, when Ti is contained, the powdering resistance is only slightly decreased with the increase of the coating amount, and only cracks occur at the coating amount of 110 g / m 2 , and there is almost no problem in practical use. The range can be expanded. In this FIG. 2, x is Ti content 0.0070 wt%,
○ indicates that the Ti content is 0 wt%.
第３図は合金化めっき層中の鉄含有量と耐パウダリング
性の関係に及ぼすＴi含有の影響を示し(片面付着量５０
g/m2。)、Ｔiを含有しない場合、鉄含有量の増加と共に
耐パウダリング性は急激に劣化するが、Ｔiを含有する
場合、鉄含有量の増加と共に耐パウダリング性は若干低
下するに留どまる。そのため合金化操業条件の管理範囲
が拡大し、品質の安定性および歩留りが著しく向上す
る。この第３図において、×はＴi含有量 0.0070wt％、
○はＴi含有量 0wt％を示す。Fig. 3 shows the effect of Ti content on the relationship between the iron content in the alloyed plating layer and the powdering resistance (the amount of deposit on one side 50
g / m 2 . ), When Ti is not contained, the powdering resistance is rapidly deteriorated as the iron content is increased, but when Ti is contained, the powdering resistance is slightly decreased as the iron content is increased. Therefore, the control range of alloying operation conditions is expanded, and the quality stability and the yield are significantly improved. In FIG. 3, x indicates a Ti content of 0.0070 wt%,
○ indicates a Ti content of 0 wt%.
実施例 ２ Ａｌ0.15wt％を含有し、Ｐbを含有しないめっき浴に、
Ｔiを 0.0070wt％を含有させた場合と含有させない場合
において、溶融めっきおよび合金化処理を実施した。Example 2 In a plating bath containing 0.15 wt% Al and containing no Pb,
Hot-dip plating and alloying treatments were carried out with and without the addition of 0.0070 wt% Ti.
得られためっき層の含有成分と含有割合および耐パウダ
リング性を第２表に示す。Table 2 shows the content and proportion of the obtained plated layer and the powdering resistance.
この第２表より、Ｔiを含有することにより耐パウダリ
ング性は著しく向上していることがわかる。It can be seen from Table 2 that the powdering resistance is remarkably improved by containing Ti.
［発明の効果］ 以上説明したように、本発明に係る合金化溶融亜鉛めっ
き鋼板は上記の構成であるから、極めて優れた耐パウダ
リング性を有するという効果がある。 [Effects of the Invention] As described above, since the galvannealed steel sheet according to the present invention has the above-mentioned configuration, it has an effect of having extremely excellent powdering resistance.
第１図は合金化めっき層中のＴi含有量と耐パウダリン
グ性の関係を示す図、第２図はめっき付着量と耐パウダ
リング性の関係に及ぼすＴi含有の影響を示す図、第３
図は合金化めっき層中鉄含有量と耐パウダリング性の関
係に及ぼすＴi含有の影響を示す図である。FIG. 1 is a diagram showing the relationship between the Ti content in the alloyed plating layer and the powdering resistance, and FIG. 2 is a diagram showing the effect of the Ti content on the relationship between the coating weight and the powdering resistance.
The figure shows the effect of Ti content on the relationship between the iron content in the alloyed plating layer and the powdering resistance.
Claims (2)
を含有し、残部Ｚnおよび不可避不純物よりなる合金化
めっき層を有することを特徴とする合金化溶融亜鉛めっ
き鋼板。1. Al 0.05-70 wt%, Ti 0.0002-0.5 wt%
And a galvannealed steel sheet containing the balance Zn and unavoidable impurities.
％、Ｐｂ1.0wt％以下 を含有し、残部Ｚnおよび不可避不純物よりなる合金化
めっき層を有することを特徴とする合金化溶融亜鉛めっ
き鋼板。2. Al0.05-70 wt%, Ti0.0002-0.5 wt
%, Pb of 1.0 wt% or less, and an alloyed hot-dip galvanized steel sheet having an alloyed plating layer composed of the balance Zn and unavoidable impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61208800A JPH0639679B2 (en) | 1986-09-04 | 1986-09-04 | Steel sheet with galvannealed alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61208800A JPH0639679B2 (en) | 1986-09-04 | 1986-09-04 | Steel sheet with galvannealed alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS6365061A JPS6365061A (en) | 1988-03-23 |
| JPH0639679B2 true JPH0639679B2 (en) | 1994-05-25 |
Family
ID=16562328
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61208800A Expired - Fee Related JPH0639679B2 (en) | 1986-09-04 | 1986-09-04 | Steel sheet with galvannealed alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0639679B2 (en) |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS58221247A (en) * | 1982-06-15 | 1983-12-22 | Nippon Soda Co Ltd | Zn-al-ti alloy for hot dipping |
| JPH0627316B2 (en) * | 1986-01-24 | 1994-04-13 | 株式会社神戸製鋼所 | Method for producing steel sheet with alloyed molten zinc plating |
-
1986
- 1986-09-04 JP JP61208800A patent/JPH0639679B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPS6365061A (en) | 1988-03-23 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| LAPS | Cancellation because of no payment of annual fees |