JPS5950952A - Mold for continuous casting - Google Patents
Mold for continuous castingInfo
- Publication number
- JPS5950952A JPS5950952A JP16060182A JP16060182A JPS5950952A JP S5950952 A JPS5950952 A JP S5950952A JP 16060182 A JP16060182 A JP 16060182A JP 16060182 A JP16060182 A JP 16060182A JP S5950952 A JPS5950952 A JP S5950952A
- Authority
- JP
- Japan
- Prior art keywords
- mold
- continuous casting
- plating layer
- molten steel
- alloy
- 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
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/04—Continuous casting of metals, i.e. casting in indefinite lengths into open-ended moulds
- B22D11/059—Mould materials or platings
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Continuous Casting (AREA)
- Electroplating Methods And Accessories (AREA)
Abstract
Description
【発明の詳細な説明】
本発明は連続鋳造用鋳型に係り、特に鋳込速度の高速化
に対応できる耐熱性、耐摩耗性のすぐれた連続鋳造用鋳
型に関する。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to a continuous casting mold, and more particularly to a continuous casting mold that has excellent heat resistance and abrasion resistance and can cope with increased casting speeds.
連続鋳造用鋳型は互に対向して配置された1組Q、鋳型
長辺と、該鋳型長辺間に挾持され進退する1組の鋳型短
辺より成り、バックプレートとの間が強制水冷され鋳型
に注入された溶鋼を迅速に抜熱するため畑もしくは銅合
金より成る鋳型基体上にニッケルもしくはニッケル合金
めつきを施したもυが使用され、更に通常ニッケルもし
くはニッケル合金めっきの第1層上に第2層としてクロ
ムめっきを施し、凝固殻の下降に対応する耐摩耗性を付
与していることは周知のとおりである。A continuous casting mold consists of a set of Q and long sides of the mold that are arranged opposite to each other, and a set of short sides of the mold that are held between the long sides of the mold and move forward and backward, and are forcedly cooled with water between them and the back plate. In order to quickly remove the heat from the molten steel poured into the mold, a mold base made of copper alloy or copper alloy is coated with nickel or a nickel alloy. It is well known that chromium plating is applied as a second layer to impart wear resistance that corresponds to the descent of the solidified shell.
しかしながら最近連続鋳造設備V大型化に伴って鋳込速
度も高速化されることにょ9ニツケルもしくはニッケル
合金のめつき層に塑性変形もしくは軟化状態が発生し、
更に鋳片を形成する凝固殻の下降およびスラブ幅変更に
伴なう鋳型短辺υ進退によって鋳型長辺に深い横疵が発
生し、更にこれらの疵によって溶鋼による溶着欠損が誘
発され著しく鋳型寿命を短縮するという問題を生じてい
る。However, as continuous casting equipment has recently become larger and casting speeds have increased, plastic deformation or softening occurs in the plated layer of nickel or nickel alloy.
Furthermore, deep horizontal flaws occur on the long side of the mold due to the descent of the solidified shell that forms the slab and the advancement and retreat of the short side of the mold due to the change in slab width.Furthermore, these flaws induce welding defects due to molten steel, significantly shortening the life of the mold. This creates the problem of shortening the .
本発明υ目的は、連続鋳造用鋳型における一ヒ記従来技
術の欠点を解消し鋳込速度の高速化にも対応し得るすぐ
れた耐熱性、耐摩耗性を有する連続鋳造用鋳型を提供す
るにある。An object of the present invention is to provide a continuous casting mold having excellent heat resistance and wear resistance, which eliminates the drawbacks of the prior art as described above, and which can cope with higher casting speeds. be.
本発明υ要旨とするところは次り如くである。The gist of the present invention is as follows.
すなわち、対向して配置された1組の鋳型長辺と該鋳型
長辺間に挾持されて進退する1組の鋳型短辺とを構成す
る銅もしくは銅合金より成る鋳型基体と、前記鋳型基体
の表面上にめっきされたニッケルもしくはニッケル基合
金より成る被覆層とを有して成る連続鋳造用鋳型におい
て、前記鋳型内υ溶鋼湯面より少くとも上方へ50rr
rm、下方へ300℃mrl)領域内υ前記鋳型長辺表
面に重量比にてタ/グステ/:3〜10チ、鉄:2〜1
0チを含み残部はニッケルもしくはニッケル基合金より
成る被覆層を有することを特徴とする連続鋳造用鋳型で
ある。That is, a mold base made of copper or a copper alloy constitutes a pair of mold long sides arranged to face each other and a set of mold short sides that move forward and backward while being held between the long sides of the mold, and a mold base of the mold base. In a continuous casting mold having a coating layer made of nickel or a nickel-based alloy plated on the surface, at least 50 rr above the molten steel surface in the mold.
rm, downward to 300°C mrl) region υ on the long side surface of the mold in weight ratio: 3 to 10 inches, iron: 2 to 1
This continuous casting mold is characterized in that it has a coating layer including nickel and the remainder made of nickel or a nickel-based alloy.
本発明者らは最近の大型連鋳設備による鋳込速度υ高速
化に伴なう鋳型寿命の短縮の原因を調査した結果、特に
鋳型のメニスカス部が最も高温であることからスラブ鋳
片の幅変更に伴なう鋳型短辺の進退によって挾持してい
る鋳型長辺の短辺進退部分が摩擦によって横抗が集中発
生し、その疵も他の部分より深いことが判明した。更に
これらυ疵が高温の溶鋼に接触することによって溶着欠
損を招く結果となり著しく鋳型の寿命を短縮する原因と
なっていることが明らかになった。The present inventors investigated the cause of the shortening of mold life due to the increase in pouring speed υ with recent large-scale continuous casting equipment, and found that the meniscus of the mold is at the highest temperature, so the width of the slab slab It was found that horizontal drag was concentrated due to friction at the part where the short side of the long side of the mold was clamped as the short side of the mold moved back and forth due to the change, and that the flaw was deeper than other parts. Furthermore, it has become clear that these υ defects cause weld defects when they come into contact with high-temperature molten steel, which significantly shortens the life of the mold.
本発明者らはこの対策について調査研究を行った結果、
これらの鋳型長辺りメニスカス部に相当する湯面部に発
生する障害を防止するためには、高温下の連続使用によ
っても塑性変形や軟化を来たすことなく長期間の使用に
十分耐える高部特性のすぐれた共析強化型電気めっきを
鋳型表面、少くともメニスカス部υ上下に相当する鋳型
長辺に施すことが最も効果的であるとの結論に達し種々
実験を重ねた結果本発明を完成するに至ったものである
。The inventors conducted research on this countermeasure and found that
In order to prevent problems that occur in the hot water surface area, which corresponds to the meniscus area around the length of the mold, it is necessary to develop a mold with excellent high-part properties that can withstand long-term use without causing plastic deformation or softening even when used continuously at high temperatures. We came to the conclusion that it is most effective to apply eutectoid-strengthening electroplating to the surface of the mold, at least to the long sides of the mold corresponding to the top and bottom of the meniscus υ.After conducting various experiments, we were able to complete the present invention. It is something that
本発明は従来の銅もしくは銅合金v鋳型基体表面上に施
されたニッケルもしくはニッケル基合金より成るめっき
層0表面に更にW:5〜1o係、Fe:2〜10係を含
み残部はNiもしくはN1基合金より成る共析強化型電
気めっきの被覆層を有する鋳型である。本発明による被
覆層の成分組成の限定理由は次の如くである。The present invention is a plating layer made of nickel or nickel-based alloy applied on the surface of a conventional copper or copper alloy V mold substrate, and further contains W: 5 to 1o and Fe: 2 to 10, and the remainder is Ni or This mold has a eutectoid-strengthened electroplated coating layer made of an N1-based alloy. The reasons for limiting the composition of the coating layer according to the present invention are as follows.
N i −W光電気めっき層は結晶粒の微細な共析強化
型めっきであり、Wの含有量が重fI:比で3%以上で
その効果が認められ、10チでその効果が飽和するので
3〜10チの範囲に限定した。The Ni-W photoelectroplated layer is a eutectoid-strengthened plating with fine crystal grains, and its effect is recognized when the W content is 3% or more in terms of weight fI: ratio, and the effect is saturated at 10 g. Therefore, it was limited to a range of 3 to 10 inches.
而して本発明の目的を達成する効果は上記N1−Wの共
析と同時にFeを共析させることによって更に顕著にな
ることを見出した。例えばFeを2チ共電析させると、
Feを共析させないめっき層υ硬度はHvにて約300
であるのに対して約38 QHv4で増加する。このF
eを共析させる場合の効果は2チ以上で認められ、次第
に増加するが10チでその効果が飽和し、かつ10%を
越すと電析層の脆化を来たすので2〜10チに限定した
。It has been found that the effect of achieving the object of the present invention becomes even more remarkable by eutectoiding Fe simultaneously with the eutectoiding of N1-W. For example, when two pieces of Fe are co-electrodeposited,
The hardness of the plating layer that does not eutectoid Fe is approximately 300 in Hv.
, it increases at about 38 QHv4. This F
The effect of co-depositing e is observed at 2 or more chips, and gradually increases, but the effect is saturated at 10 chips, and if it exceeds 10%, the deposited layer becomes brittle, so it is limited to 2 to 10 chips. did.
またFeを共析させる効果は高温強度にも顕著であって
、例えばN1−W電析層では500℃を越えると軟化を
開始するが、Fe:2〜10%を共析させると軟化開始
温度が600℃まで上昇すると共に、600℃において
も初期の約60チの強度を保持することが判明した。The effect of eutectoiding Fe is also remarkable in high-temperature strength; for example, a N1-W deposited layer starts to soften when the temperature exceeds 500°C, but when 2 to 10% Fe is eutectoid, the softening temperature It was found that the initial strength of about 60 degrees was maintained even at 600 degrees Celsius as the temperature rose to 600 degrees Celsius.
次に上記Ni −W −FeQ共析ノーを施す鋳型り位
置について述べる。こV) N i −W −Fe (
Q共析層を鋳型υ長辺、短辺υ全面に施すことは効果的
には最善であるが、非常に高価となるってコストとも考
え併せ最も効果的な共析層実施位置を決定することとし
た。Next, the mold position where the Ni-W-FeQ eutectoid is applied will be described. V) N i -W -Fe (
QIt is effectively best to apply the eutectoid layer to the entire long side and short side υ of the mold, but it is very expensive, so consider the cost and decide the most effective position to apply the eutectoid layer. I decided to do so.
先ず鋳型銅板の表面よシ20mm深さQ鋳込速度1、0
m / n1inの時の温度分布を調査したところ第
1図に示す如き結果を得た。第1図より明らかなとおり
、鋳型上端がら約2ooITII′rl、メニスカスよ
シ約10011′+mの位置が温度が最も高く約250
Cに達し鋳型の下部に至るに従い銅板的震度が低下して
いること、および鋳込中のスラブ幅変更時、鋳型短辺を
進退させることによる摩擦によって鋳型長辺に横抗が生
じ、この横抗鏡高u1溶鋼と溶着しめつき層に欠損を生
じ鋳型寿命を著しく短縮している事実より本発明にょる
N1−W−FeD共析めつき層の効果的な要めっき部分
は鋳型長辺の溶鋼湯面のメニスカス部よシ少くとも上方
へ50mm、下方へ300前lの領域内にめっきを施す
べきである。First, the surface of the mold copper plate is 20mm deep, Q the casting speed is 1, 0.
When the temperature distribution at m/n1in was investigated, the results shown in FIG. 1 were obtained. As is clear from Figure 1, the temperature is highest at about 2ooITII'rl from the upper end of the mold and about 10011'+m from the meniscus, at about 250 m.
The seismic intensity of the copper plate decreases as it reaches C and reaches the bottom of the mold, and when changing the width of the slab during pouring, the friction caused by moving the short side of the mold back and forth causes horizontal resistance on the long side of the mold. Due to the fact that the anti-mirror high u1 molten steel causes defects in the welded fastening layer and significantly shortens the mold life, the effective plating area of the N1-W-FeD eutectoid plating layer according to the present invention is on the long side of the mold. Plating should be applied within an area of at least 50 mm above the meniscus of the molten steel surface and 300 mm below.
こυ領域内で更に最小限を望む場合は、第2図にて示す
如く鋳型短辺の進退部分に限定してもよい。なお、本発
明によるNi −W −Feめつき層の厚みは50μm
n程度で十分である。If a further minimum is desired within this υ region, it may be limited to the advancing and retreating portions of the short sides of the mold, as shown in FIG. The thickness of the Ni-W-Fe plating layer according to the present invention is 50 μm.
About n is sufficient.
実 方亀 列
断面形状が厚さ17Onvnx幅1.800 manの
スラブ鋳片の連続鋳造において、鋳込回数320チヤー
ジ使用後の従来の通常のNiめつきを施した鋳型と、本
発明による8 9 %Ni−71W−4%Fe (7)
めっきを第2[?21(A)、 (B)に示す如く鋳型
長辺2のメニスカス部より上方へ50mm、下方へ20
01TllTIOみとし、中央部を除いて鋳型短辺の進
退部分に施し、スラブ鋳片0幅を1800mmから12
00mmへの縮小および1200mmから1800+T
Imへ0幅拡大を50回実施した後の鋳型長辺2上に発
生した疵の深さおよび疵発生量を比較調査した。In the continuous casting of a slab slab with a row cross-sectional shape of 17 mm in thickness and 1.800 mm in width, a conventional conventional mold with Ni plating after 320 castings and a mold according to the present invention were used. %Ni-71W-4%Fe (7)
Plating the second [? 21 (A), (B), 50 mm above and 20 mm below the meniscus part of long side 2 of the mold.
01TllTIO was applied to the advancing and retracting parts of the short sides of the mold except for the center part, and the width of the slab slab was changed from 1800 mm to 12
Reduction to 00mm and 1200mm to 1800+T
The depth of the flaws generated on the long side 2 of the mold and the amount of flaws generated after 50 times of zero-width expansion to Im were compared and investigated.
こつ場合υ本発明によるめっきは第2図(B)に示す如
く、鋳型基体4の銅板上の最小限領域に一定厚みυNi
めつき6を施し、更にそ0表面に本発明によるN1−W
−Feめつき8を5Q7anノq実施し、そυ他υ部分
!(はN1めつきを施して表面が均一になるようにした
もっである。In the case of plating according to the present invention, a constant thickness of υNi is applied to the minimum area on the copper plate of the mold base 4 as shown in FIG.
Plating 6 is applied, and N1-W according to the present invention is applied to the 0 surface.
-Fe plating 8 was carried out on 5Q7annoq, and other υ parts! (This is one that has been plated with N1 to make the surface uniform.
本発明によるN1−W−Feめつき層8の施行態様は上
記υほか、第2図(qに示す如く直接鋳型基体4v銅板
上に施し、その他υ部分はNiめつき6としてもよい。The N1-W-Fe plating layer 8 according to the present invention can be applied in addition to the above-mentioned υ, as shown in FIG.
上記比較試験の結果、従来法によるNiめつきのみV場
合には最大深さ約05〜1.0 mmの欠損部が多数間
められたのに対し、本発明による鋳型においては疵8/
)深さは最大約0.02nrmであり、発生量も半減し
ていることが認められた。なお、本発明による鋳型はそ
の後使用を継続したが、最終的に従来の鋳型に比し寿命
が2缶板−Hに延長された。As a result of the above comparative test, many defects with a maximum depth of approximately 0.5 to 1.0 mm were created in the case of only Ni plating using the conventional method, whereas in the case of the mold according to the present invention, there were 8/8 defects.
) The maximum depth was approximately 0.02nrm, and it was observed that the amount generated was also halved. Although the mold according to the present invention continued to be used after that, its lifespan was finally extended to 2 can plates-H compared to the conventional mold.
上記実施例より明らかなとおり、本発明による連続鋳造
用鋳型は、従来の鋳型基体の銅板上に直接もしくは銅板
上にNiめっきを施し、更にそ0表面−ヒにW;3〜1
0%、Fe:2〜10%、残シNiもしくはNi基合金
より成る共析強化型電気めつきを施し、その実施領域を
少くとも鋳型湯面υ上方50IrIITl、下方へ30
0mmとしたつで次の如き効果を収めることができた。As is clear from the above examples, the continuous casting mold according to the present invention has Ni plating applied directly to or on the copper plate of the conventional mold base, and further has a W of 3 to 1 on the surface.
0%, Fe: 2 to 10%, balance Ni or Ni-based alloy eutectoid-strengthened electroplating is applied, and the application area is at least 50 IrIITl above the mold surface and 30 IrIITl below.
By setting it to 0 mm, the following effects could be achieved.
(イ)@!造するスラブ鋳片の頻繁な幅変更による短辺
進退によっても従来り如き横抗の発生は極めて微少であ
って鋳型寿命を従来v2倍以上に延長することができた
。(stomach)@! Even though the width of the slab slab to be manufactured is changed frequently and the width of the short side is moved back and forth, the occurrence of horizontal drag as in the conventional method is extremely small, and the life of the mold can be extended by more than twice that of the conventional method.
沖)本発明による鋳型は、従来の如きめっき層Q塑性変
形、軟化状態の発生が完全に解消され、すぐれた4熱性
と耐摩耗性を有しているので、今後ryfIJJ型の大
型化、鋳込速度の高速化にも十分対応することができる
。Oki) The mold according to the present invention completely eliminates the occurrence of plastic deformation and softening of the plating layer Q as in the past, and has excellent heat resistance and wear resistance. It can also fully cope with the increase in loading speed.
(ハ)本発明によるN1−W−Feめつき層の実施部位
を鋳型長辺の最少必要限度領域に限定すれば、施行費用
も比較的少くてすむって効果によって十分償い得る。(c) If the area where the N1-W-Fe plating layer is applied according to the present invention is limited to the minimum necessary area on the long side of the mold, the cost of implementation can be relatively small and can be fully compensated for by the effect.
第1図は連続鋳造における鋳型銅板内の鋳型上端から測
定した温度分布図、第2図(5)、 (B)、 (C)
は本発明の実施例におけるN i −W −Feめつき
層を施す鋳型長辺部位を示し、(A)はその正面斜視図
、CB)は四回のB−B線矢視断面図、(C)はB−B
線矢視断面図の他の態様を示す。
2・・・鋳型長辺、 4・・・鋳型基体6・・・
Niめつき層 8・・・N1−W−Feめつき層代理
人 弁理士 中 路 武 雄
第1図
i
1コシ!P金同オ反3Fし1蓼ミ (0C)(A)Figure 1 is a temperature distribution diagram measured from the upper end of the mold in the mold copper plate during continuous casting, Figure 2 (5), (B), (C)
(A) is a front perspective view thereof, (CB) is a sectional view taken along the line B-B four times, ( C) is B-B
Another aspect of the line arrow sectional view is shown. 2... Mold long side, 4... Mold base 6...
Ni-metsuki layer 8...N1-W-Fe-metsuki layer agent Patent attorney Takeo Nakaji Figure 1 i 1 kosi! P gold dougou 3F shi1 taedami (0C) (A)
Claims (1)
長辺間に挾持されて進退する1組の鋳型短辺とを構成す
る銅もしくは銅合金より成る鋳型基体と、前記鋳型基体
の表面上にめっきされたニッケルもしくはニッケル基合
金より成る被覆層とを有して成る連続鋳造用鋳型におい
て、前記鋳型内の溶鋼湯面より少くとも−F方へ50m
m、下方へ300胴の領域内の前記鋳型長辺表面に重量
比にてタ/グヌテ/:3〜10チ、鉄:2〜10%を含
み残部はニッケルもしくはニッケル基合金より成る被覆
層を有することを特徴とする連続鋳造用鋳型。(1) A mold base made of copper or copper alloy, which constitutes a pair of mold long sides arranged to face each other and a set of mold short sides that move forward and backward while being sandwiched between the long sides of the mold, and the mold base a continuous casting mold having a coating layer made of nickel or a nickel-based alloy plated on the surface of the continuous casting mold, at least 50 m in the -F direction from the molten steel surface in the mold.
m, downwardly on the long side surface of the mold in the region of 300 cylinders, a coating layer containing 3 to 10% by weight, iron: 2 to 10%, and the remainder consisting of nickel or a nickel-based alloy. A continuous casting mold comprising:
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP16060182A JPH0235619B2 (en) | 1982-09-14 | 1982-09-14 | RENZOKUCHUZOYOIGATA |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP16060182A JPH0235619B2 (en) | 1982-09-14 | 1982-09-14 | RENZOKUCHUZOYOIGATA |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS5950952A true JPS5950952A (en) | 1984-03-24 |
JPH0235619B2 JPH0235619B2 (en) | 1990-08-13 |
Family
ID=15718464
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP16060182A Expired - Lifetime JPH0235619B2 (en) | 1982-09-14 | 1982-09-14 | RENZOKUCHUZOYOIGATA |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH0235619B2 (en) |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS60145247A (en) * | 1983-12-29 | 1985-07-31 | Kawasaki Steel Corp | Mold for continuous casting and its production |
JPS60221151A (en) * | 1984-04-18 | 1985-11-05 | Kawasaki Steel Corp | Continuous casting mold and formation of thermally sprayed film on inside surface of mold |
KR100430420B1 (en) * | 1998-09-04 | 2004-07-27 | 주식회사 제이테크 | Method for plating Mold Win on a Continuous Casting Mold |
US7896061B2 (en) | 2005-02-02 | 2011-03-01 | Nomura Plating Co., Ltd. | Product having improved zinc erosion resistance |
-
1982
- 1982-09-14 JP JP16060182A patent/JPH0235619B2/en not_active Expired - Lifetime
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS60145247A (en) * | 1983-12-29 | 1985-07-31 | Kawasaki Steel Corp | Mold for continuous casting and its production |
JPS6351787B2 (en) * | 1983-12-29 | 1988-10-17 | Kawasaki Seitetsu Kk | |
JPS60221151A (en) * | 1984-04-18 | 1985-11-05 | Kawasaki Steel Corp | Continuous casting mold and formation of thermally sprayed film on inside surface of mold |
JPH0337454B2 (en) * | 1984-04-18 | 1991-06-05 | Kawasaki Steel Co | |
KR100430420B1 (en) * | 1998-09-04 | 2004-07-27 | 주식회사 제이테크 | Method for plating Mold Win on a Continuous Casting Mold |
US7896061B2 (en) | 2005-02-02 | 2011-03-01 | Nomura Plating Co., Ltd. | Product having improved zinc erosion resistance |
AU2006211677B2 (en) * | 2005-02-02 | 2011-03-31 | Nomura Plating Co., Ltd. | Product having improved zinc erosion resistance |
Also Published As
Publication number | Publication date |
---|---|
JPH0235619B2 (en) | 1990-08-13 |
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