JPS5822330A - Production of cold-rolled ferritic stainless steel sheet excellent in formability and surface brightness - Google Patents
Production of cold-rolled ferritic stainless steel sheet excellent in formability and surface brightnessInfo
- Publication number
- JPS5822330A JPS5822330A JP12063281A JP12063281A JPS5822330A JP S5822330 A JPS5822330 A JP S5822330A JP 12063281 A JP12063281 A JP 12063281A JP 12063281 A JP12063281 A JP 12063281A JP S5822330 A JPS5822330 A JP S5822330A
- Authority
- JP
- Japan
- Prior art keywords
- rolling
- cold
- rolled
- steel sheet
- recrystallization
- 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.)
- Pending
Links
- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 17
- 238000004519 manufacturing process Methods 0.000 title claims description 9
- 238000005096 rolling process Methods 0.000 claims abstract description 96
- 238000005097 cold rolling Methods 0.000 claims abstract description 60
- 238000000137 annealing Methods 0.000 claims abstract description 27
- 238000001953 recrystallisation Methods 0.000 claims abstract description 18
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 16
- 239000010959 steel Substances 0.000 claims abstract description 14
- 238000005554 pickling Methods 0.000 claims abstract description 10
- 238000000034 method Methods 0.000 claims description 47
- 238000005498 polishing Methods 0.000 claims description 14
- 238000009792 diffusion process Methods 0.000 claims description 7
- 238000012360 testing method Methods 0.000 claims description 3
- 239000010960 cold rolled steel Substances 0.000 abstract description 13
- 238000005422 blasting Methods 0.000 abstract description 2
- 239000000314 lubricant Substances 0.000 abstract 4
- 239000002253 acid Substances 0.000 abstract 1
- 230000003746 surface roughness Effects 0.000 description 10
- 238000007796 conventional method Methods 0.000 description 8
- 239000000463 material Substances 0.000 description 8
- 239000010935 stainless steel Substances 0.000 description 5
- 238000010586 diagram Methods 0.000 description 4
- 238000007517 polishing process Methods 0.000 description 4
- 238000012545 processing Methods 0.000 description 4
- 239000010731 rolling oil Substances 0.000 description 4
- 239000002184 metal Substances 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 230000001105 regulatory effect Effects 0.000 description 3
- 239000003795 chemical substances by application Substances 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 150000002739 metals Chemical class 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- 230000000007 visual effect Effects 0.000 description 2
- 239000004372 Polyvinyl alcohol Substances 0.000 description 1
- 241000287531 Psittacidae Species 0.000 description 1
- 239000003082 abrasive agent Substances 0.000 description 1
- 239000006061 abrasive grain Substances 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 210000000988 bone and bone Anatomy 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 238000005553 drilling Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 210000003608 fece Anatomy 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 239000010871 livestock manure Substances 0.000 description 1
- 238000005461 lubrication Methods 0.000 description 1
- 238000000691 measurement method Methods 0.000 description 1
- 229920002451 polyvinyl alcohol Polymers 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000004439 roughness measurement Methods 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 230000002747 voluntary effect Effects 0.000 description 1
- 238000005406 washing Methods 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B3/02—Rolling special iron alloys, e.g. stainless steel
-
- 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 by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing of ferrous alloys
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Metal Rolling (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Description
【発明の詳細な説明】
本発明は穴拡げ成形性、深絞り成形性などの成形性と表
面光沢に優れ穴フェライト系ステンレス鋼冷延鋼板の製
造法K11する。DETAILED DESCRIPTION OF THE INVENTION The present invention is directed to a method K11 for producing a cold-rolled stainless steel sheet with holes having excellent formability such as hole expansion formability and deep drawing formability, and surface gloss.
8U8450によって代表される汎用のフェライト系ス
テンレス鋼は比較的安価であり、その冷延鋼板は、建築
内装材9日常器具、厨房設置llに流し)0種々の装飾
品9球面反射鏡等の用途に使用されている。比等の用途
に適するためKは、該鋼板は穴拡げ成形性、深絞り成形
性などの成形性が良好であると同時に優れた表面光沢性
を有しなければならない。General-purpose ferritic stainless steel, represented by 8U8450, is relatively inexpensive, and its cold-rolled steel sheets are used in architectural interior materials, daily appliances, kitchen equipment, and various decorative items, such as spherical reflectors. It is used. In order for K to be suitable for applications such as ratios, the steel sheet must have good formability such as hole expansion formability and deep drawing formability, as well as excellent surface gloss.
しかしながら、フェライト系ステンレス鋼の熱延鋼帯か
ら所定板厚の冷延鋼板に仕上げる技術上からいえば、上
述の成形性と表面光沢性とは両立しKくい特性である。However, from a technical standpoint of finishing a hot-rolled steel strip of ferritic stainless steel into a cold-rolled steel sheet of a predetermined thickness, the above-mentioned formability and surface gloss are characteristics that are difficult to coexist with.
一般にこの二つの特性は冷間圧延の圧延率に関係があり
、成形性の指標である穴拡げ比は通常−次冷間圧延と仕
上冷間圧延からなる冷間圧延のうち、仕上冷間圧延の圧
延率の増加とともに低下し、逆に表面光沢性は、仕上冷
間圧延の圧延率の増加とともに向上する。従って両特性
を兼ね備えた冷延鋼板を得ることは技術上困難である。In general, these two characteristics are related to the rolling rate of cold rolling, and the hole expansion ratio, which is an index of formability, is usually surface glossiness decreases as the rolling rate increases, and conversely, surface gloss improves as the rolling rate of finish cold rolling increases. Therefore, it is technically difficult to obtain a cold-rolled steel sheet that has both properties.
にもかかわらずこの相客れない二つの特性を共に高度K
ll、tJ製品への、過酷とも思われる要求が近来一般
的傾向となっている。Nevertheless, these two incompatible characteristics are both highly K.
ll, tJ There has been a general trend in recent years to place seemingly harsh demands on products.
従来の通常の製造法によって得られたフェライト系ステ
ンレス鋼冷延鋼板は、満足な穴拡げ成形加工ができず、
ノンチング+切削加工による開口部をポンチで押し拡げ
る時に打抜面または切削面に割れが発生して製品として
使用できないことが多々あった。tたとの穴拡げ成形加
工と同時にまたはその前後に探絞り成形加工が実施され
る場合が多いがフェライト系ステンレス鋼冷延鋼板は周
知のように一般に深絞り成形性が悪い。Ferritic stainless steel cold-rolled steel sheets obtained by conventional conventional manufacturing methods cannot be satisfactorily expanded and formed.
There were many cases where cracks occurred on the punched or cut surface when expanding the openings created by nonching + cutting with a punch, making the product unusable. Detection drawing is often carried out at the same time as or before or after the hole expansion forming process, but as is well known, ferritic stainless steel cold rolled steel sheets generally have poor deep drawability.
このように成形性が劣ることはフェライト系ステンレス
鋼冷延鋼板にとって非常にやっかいな問題であり、さら
に前述の装飾品1球面反射鏡のような用途に4供し得る
優れた表面光沢性をも確保す・ることけ、さらに技術上
の困難を伴なう。This poor formability is a very troublesome problem for cold-rolled ferritic stainless steel sheets, and it also ensures excellent surface gloss that can be used for applications such as the above-mentioned ornaments 1 and spherical reflectors. However, it is accompanied by further technical difficulties.
リング処理(機械的スケール除去を含む酸洗)シ。Ring treatment (pickling including mechanical descaling).
粗研摩(通常ベルトグラインダーによる)シ。Rough sanding (usually with a belt grinder).
45〜60%の一次冷間圧延を施し、再結晶焼鈍酸洗し
、60〜8096の仕上冷間圧延を施してから、光輝焼
鈍し無潤滑調質圧延(通常圧延″$0.8〜1.8 %
)する方法が取られていた(第FZ1図参照)。第f
41図で示す従来方法、第172図で示す比較的最近の
直前従来技術及び第2図で示す本願発明方法において、
いずれに、を共通することであるが、−次冷関圧′延、
仕上冷関圧延の冷間圧延ハ9周知のコールドタンデムミ
ル、センジミア・ミル等によって行なわれ9次いで調質
圧延も同様に周知の2重もしくは4重圧延機であって作
業ロール直径が400〜900重程度の比較的大径ロー
ルを用い更に該ロール表面粗1が8.1〜(15μ程変
の非常に光沢のある硬式ロールを用いてなされる。この
場合、無潤滑調質圧延とは(勿論周知であるが)、上記
圧延機で0文字通シ無潤滑の状II(ドライな状II)
で調質圧延を行なうこトチ、作業ロールとステンレス鋼
冷延鋼帯即ち金属同志が直接接触する圧延であって、冷
延鋼帯の調質は当然行われるが、圧延理論に云うスリッ
ピング現象により表面光沢が増すことを特徴とするもの
である。(なお第171.f’〆2.’=3図において
*は拡散焼鈍を施し穴かまた施こさない熱延鋼帯を意味
する。)
比較的最近には上記の方法を改良して、−次冷間圧延の
圧延率を75〜80嘔に上げ、仕上冷間圧延の前に軽研
摩工程(通常番1000砥粉による研磨)を挿入し、仕
上冷間圧延の圧延率を37〜44慢に下げる方法が行わ
れ(第77”2図参照)。After performing primary cold rolling of 45-60%, recrystallization annealing and pickling, and final cold rolling of 60-8096, bright annealing and non-lubricated temper rolling (normal rolling"$0.8-1 .8%
) (see Figure FZ1). fth
In the conventional method shown in FIG. 41, the relatively recent prior art shown in FIG. 172, and the method of the present invention shown in FIG.
What they all have in common is - cold rolling,
The cold rolling of finishing cold rolling is carried out by a well-known cold tandem mill, Sendzimir mill, etc.9 The temper rolling is similarly carried out by a well-known double or quadruple rolling mill with a work roll diameter of 400 to 900 mm. It is carried out using a relatively large-diameter heavy roll and a very glossy hard roll with a surface roughness of 8.1 to 15 μm. In this case, non-lubricated temper rolling is Of course, this is well known), but the above rolling mill has zero lubrication condition II (dry condition II).
Temper rolling is a rolling process in which the work rolls and cold rolled stainless steel strips, that is, metals come into direct contact with each other, and the cold rolled steel strips are naturally tempered, but the slipping phenomenon described in rolling theory occurs. It is characterized by an increase in surface gloss. (Note that in Figure 171.f'〆2.'=3, * means a hot rolled steel strip that has undergone diffusion annealing or not.) Relatively recently, the above method has been improved, - The rolling rate of the next cold rolling was increased to 75 to 80 mm, a light polishing process (polishing with regular No. 1000 abrasive powder) was inserted before the final cold rolling, and the rolling rate of the final cold rolling was increased to 37 to 44 mm. A lowering method is used (see Figure 77"2).
この方法では前記の二つの特性を相当に両立具備した製
品が得られるが、何分にも軽研摩工程は時間を要し、6
トンコイル1本を研摩するのに24時間を要する。With this method, a product with both of the above two properties can be obtained, but the light polishing process takes many minutes, and
It takes 24 hours to polish one ton coil.
本発明者等はこの方法の改良を目途し、軽研摩にかわる
手段として、ここに無潤滑調質圧延(通常圧延率0.5
〜5. O% )を挿入し穴ところ、優るとも劣らない
品質を維持して生産性を大いに向上することができ穴。The present inventors aim to improve this method, and as a means to replace light polishing, the present inventors used non-lubricated temper rolling (normal rolling rate of 0.5
~5. By inserting holes into holes, you can maintain superior quality and greatly improve productivity.
本発明によれば、拡散焼鈍を施しであるかt穴は施して
ない熱延鋼帯をデスケーリング処理し。According to the present invention, a hot-rolled steel strip that has been diffusion annealed or has no T-holes is descaled.
粗研摩し、75〜80嘔の圧延率で一次冷間圧延を施し
、再結晶焼鈍・酸洗し、無潤滑調質圧延を行ない、圧延
率57〜44嘔の仕上冷間圧延を行ない、再結晶光輝焼
鈍を行ない、最後に無潤滑調質圧延を行なうことからな
る成形性と表面光沢性に優れたフェライト系ステンレス
鋼冷延鋼板の製造法が提供される。Rough polishing, primary cold rolling at a rolling rate of 75 to 80 mm, recrystallization annealing and pickling, non-lubricated temper rolling, finishing cold rolling at a rolling rate of 57 to 44 mm, and re-rolling. Provided is a method for producing a cold-rolled ferritic stainless steel sheet with excellent formability and surface gloss, which comprises performing crystal bright annealing and finally non-lubricated temper rolling.
また本発明によれば、上記の方法において、第1次冷間
圧延後の再結晶焼鈍・酸洗に替えて再結晶光輝焼鈍を行
なう方法が提供される(第3図参照)。Further, according to the present invention, there is provided a method in which recrystallization bright annealing is performed in place of recrystallization annealing and pickling after the first cold rolling in the above method (see FIG. 3).
本発明方法の出発材料となる熱延鋼帯は通常拡散焼鈍を
施し食ものであるが、拡散焼鈍を施さないで直ちにデス
ケーリング処理(酸洗)して冷間圧延にまわす場合もあ
る(この方がリツジング発生の少ない冷延鋼板が得られ
るといわれている)ので、その両方を含む。本発明方法
においてデスケーリング処理とはショツトブラストとか
プロセッサー屯しくけレベラーによる繰り返し曲げ歪を
付与するなどの機械的スケール除去を含む酸洗を意味す
る。The hot-rolled steel strip, which is the starting material for the method of the present invention, is usually processed by diffusion annealing, but in some cases it is immediately descaled (pickled) and then sent to cold rolling without being subjected to diffusion annealing. (It is said that cold-rolled steel sheets with less occurrence of ripping can be obtained), so both are included. In the method of the present invention, descaling treatment means pickling that includes mechanical scale removal such as shot blasting or applying repeated bending strain using a processor-loaded leveler.
本発明の方法は大体においてフェライト系ステンレス鋼
一般に適用できるが、その効果は就中8US429,4
50.45OL!、8U8434゜5U8410Lにお
いて顕著である。The method of the present invention is generally applicable to ferritic stainless steels in general, but its effects are particularly noticeable in 8 US 429, 4
50.45OL! , 8U8434°5U8410L.
本発明の方法において一次冷関圧延率を75〜8C1に
仕上冷間圧延率を37〜4496に限定した理由は次の
通りである。The reason for limiting the primary cold rolling rate to 75-8C1 and the finishing cold rolling rate to 37-4496 in the method of the present invention is as follows.
一次冷間圧延、再結晶焼鈍、二次冷間王延および再結晶
焼鈍の工程を経ることによってフェライト系ステンレス
鋼の熱延鋼帯から所定板厚の冷延鋼板を製造する際に、
−次冷間圧延での圧延率を70〜90−にし、二次冷間
圧延の冷延率を60〜45g&にすることによって穴拡
げ成形性及び深絞り成形性の改善された冷延鋼板を得る
ことができることは、すでに本出願人の他の発明者によ
って見吊されていた。 (11?開昭54−12842
3号)が1本発明者等の研究によると、その−次および
巳次冷関圧延即ち仕上冷間圧延の圧延率の範囲内におい
て、さらに前記のように限定し、無潤滑調質圧延を製造
工程中に組み合わすことによって、成形性とともに表面
光沢性がさらに改善されることが分ったからである。When manufacturing a cold-rolled steel plate of a predetermined thickness from a hot-rolled ferritic stainless steel strip through the steps of primary cold rolling, recrystallization annealing, secondary cold rolling, and recrystallization annealing,
- A cold rolled steel sheet with improved hole expansion formability and deep drawing formability can be produced by setting the rolling rate in the secondary cold rolling to 70 to 90 - and making the cold rolling rate in the secondary cold rolling to 60 to 45g&. What could be obtained had already been envisaged by other inventors of the present applicant. (11? Kaisho 54-12842
According to research by the present inventors, No. 3) is further limited as described above, and non-lubricated temper rolling is performed within the range of the rolling rate of the next and Matsugi cold rolling, that is, finish cold rolling. This is because it has been found that by combining them during the manufacturing process, moldability and surface gloss are further improved.
この表面光沢性を増すため、換言すれば表面粗度(凹凸
)を極力小さくするため、熱延鋼帯の表面肌の改善9機
械的或いは化学的デスケーリング処理技術の改善、更に
粗研摩の簡略化(パス回数の減少、できるだけ微細砥粒
による軽研摩化)もしくけ省略化等を検討し改善した結
来、大巾な効果を上げたのであるが、おのずとその限界
があり顧客の要求度合を満足させ得す本発明の方法に至
ったのである。上記の効果を(−スとして1本発明の方
法を実施することKより9表面光沢を一層増し顧客の要
求を満足させることができるものである。In order to increase this surface glossiness, in other words, to minimize the surface roughness (unevenness), improvement of the surface texture of the hot rolled steel strip 9 Improvement of mechanical or chemical descaling treatment technology, and further simplification of rough polishing As a result of considering and improving methods such as reducing the number of passes and light polishing using as fine abrasive grains as possible, and simplifying the process, we achieved great results. The method of the present invention has been achieved which satisfies the above. By carrying out the method of the present invention based on the above effects, the surface gloss can be further increased and the customer's requirements can be satisfied.
本発明の方法において、第1ヂ2図で示され。In the method of the invention, as shown in FIGS. 1-2.
直前従来技術である仕上冷間圧延前の軽研摩に代わる手
段として無潤滑調質圧延を挿入することは。Inserting non-lubricated skin pass rolling as an alternative to light polishing before final cold rolling, which is just prior art.
既に前記したが、仕上圧延前に軽研摩或いはこれに代る
無潤滑調質圧延を挿入する理由は次のようなものである
。As already mentioned above, the reason for inserting light polishing or non-lubricated temper rolling in place of it before finish rolling is as follows.
コールドタンデムミル、センシミアミルのいずれの圧延
機によって本、比較的変形抵抗の大きなステンレス鋼の
冷間圧延においては0通常圧延油が使用されるが、この
圧延油は冷間圧延に供せられる材料表面の凹凸部の凹部
(くぼみ)Kitつたまま(或いはプールしたtま)の
状態で1作業ロールに噛み込まれる。このようKして9
作業ロールと材料表面の接触により、比等の関に封じ込
まれた圧延油は逃げ場がなくな夛、封じ込まれたまま圧
延され、圧延が完了した時(上記の接触が解かれた時)
圧延油は解放されるが、一方この圧延油がたまってい大
凹部の程変は圧延前に比較し。In the cold rolling of stainless steel, which has relatively high deformation resistance, by either rolling mills such as cold tandem mills or Senshimia mills, normal rolling oil is used. The concave part (dent) of the uneven part of the kit is caught in one work roll in the state of being stuck (or pooled). K like this 9
Due to the contact between the work roll and the material surface, the rolling oil trapped in the groove has no place to escape and continues to be rolled while being trapped, and when rolling is completed (when the above contact is broken)
The rolling oil is released, but on the other hand, this rolling oil accumulates and the shape of the large concave portion changes compared to before rolling.
スリッピング現象によシ僅かに軽減化するが殆んど変ら
ない。Although it is slightly reduced due to the slipping phenomenon, there is almost no change.
つまり、冷間圧延前の材料表面粗度(凹凸)の度合が圧
延後も殆んどそのtま残存するので、材料表面のデ沢性
をだすためKは、冷間圧延前、特に製造末端工程に近い
仕上冷間圧延前に可能な限り、材料表面の粗度を小さく
する必要がある。この手段として、軽研摩或いは無潤滑
調質圧延が採用されるのである。久に最初の無潤滑調質
圧延の圧延率を[L5〜5.0嘔であることが好ましい
の社。In other words, the degree of surface roughness (unevenness) of the material before cold rolling remains almost the same after rolling, so in order to obtain the roughness of the material surface, K is set before cold rolling, especially at the manufacturing end. It is necessary to reduce the roughness of the material surface as much as possible before finishing cold rolling near the process. Light polishing or non-lubricated temper rolling is used as a means for this purpose. The rolling rate of the first non-lubricated skin pass rolling is preferably L5 to 5.0.
以下に述べる理由による。This is due to the reasons stated below.
軽研摩に代わる調質圧延としては、少くともo、5%1
!変あることが望ましいが596程度で表面光沢は上限
に達し、これ以上の光沢向上は望めず。As a temper rolling alternative to light polishing, at least o, 5% 1
! Although it is desirable that the surface gloss be different, the surface gloss reaches its upper limit at about 596, and no further improvement in gloss can be expected.
この上限を起えると金属同志の接触である無潤滑調質圧
延であり必然的にノぞス回数もふえるため。If this upper limit is reached, the number of nozzles will inevitably increase due to non-lubricated temper rolling where metals come into contact with each other.
金属粉の発生、その他の原因によシロールが汚れ逆Kj
t、沢は失われる。この調質圧延は、1回ないし数回の
パスで行なわれているが、求められる光沢の程度と生産
性を勘案しながら調節し、できるだけ数少ないノζスで
処理することが望ましいのは云うまでもない。Reverse Kj due to generation of metal powder or other causes.
t, the stream is lost. This temper rolling is performed in one or several passes, but it goes without saying that it is desirable to adjust it while taking into account the desired degree of gloss and productivity, and to perform the process with as few passes as possible. Nor.
最後の調質圧延の圧延率[18〜12%は従来行われて
いる範囲であるが、帥工@において最終の再結晶光輝焼
鈍(軟化)が行われた後の調質圧延であるから、製品の
成形性を確保するためKも大きな圧延率をとることは好
しくなく、必要最小限に抑えるべきである。The rolling rate of the final temper rolling [18 to 12% is within the conventional range, but since this is the temper rolling after the final recrystallization bright annealing (softening) is performed in the master @, In order to ensure the formability of the product, it is not preferable to use a large rolling rate for K, and it should be kept to the minimum necessary.
本発明の方法は第3図に基本的な工程を示し。The basic steps of the method of the present invention are shown in FIG.
その詳細を以上に説明したのであるが、フェライト系ス
テンレス鋼冷延鋼板(製品)の成形性と表面光沢性を両
立具備させるため、−次及び仕上冷間圧延工程と各圧延
率の配分及び仕上冷間圧延酊の無潤滑調質圧延工程とそ
の圧延率を骨子とする吃ので即ち工程とその工程に付随
する緒条性から構成されるものである。The details have been explained above, but in order to achieve both formability and surface gloss of ferritic stainless steel cold-rolled steel sheets (products), the next and final cold rolling processes, the distribution of each rolling rate, and the finishing It consists of a non-lubricated temper rolling process of cold rolling and its rolling rate, that is, a process and characteristics associated with the process.
又本発明は、製品に両特性を具備させ乍ら、高生産性を
維持するため製造工程として最短工程を採ることが必要
であり、そのように構成されている。従来法の研摩工程
は、大規模な設備を要し。Further, the present invention is configured in such a manner that it is necessary to adopt the shortest manufacturing process in order to maintain high productivity while providing the product with both characteristics. Conventional polishing processes require large-scale equipment.
従って大きなスば一次を要し、莫大な設備投資を必要と
するのみてなく、製造原偵を上昇させるとともに研摩に
種々の物品を要し、その購入保管管理も大変であり、更
に研摩作業現場に於る作業性も悪轟く、僅か6トンコイ
ルで24時間要していた。ところが9本発明によれば上
記研摩工程の種々の問題を軽減させ、何よりも現場の作
業性を改善させ、6トンコイルも2時間で済み生産性の
増強をもたらした。大体の試算で本発明の方法は。Therefore, not only does it require a large space and a huge investment in equipment, but it also increases the number of manufacturing staff and requires a variety of materials for polishing, which is difficult to purchase, store, and manage. The work efficiency was also poor, and it took 24 hours with only 6 tons of coils. However, according to the present invention, various problems in the polishing process described above are alleviated, and above all, workability on site is improved, and a 6-ton coil can be manufactured in just 2 hours, resulting in an increase in productivity. The method of the present invention is roughly estimated.
該従来法に比して約20分の1の骨用で済み、11合的
に飛躍した生産性の増強をもたらすものである。Compared to the conventional method, the amount of bone used is approximately 1/20th, resulting in an 11-fold increase in productivity.
次に実施例によって本発明を具体的に説明する。Next, the present invention will be specifically explained with reference to Examples.
C: Q、05チー S i : [L54 ’A
e M!1:α51%。C: Q, 05 Qi S i: [L54 'A
eM! 1: α51%.
P :0.21優、S :[LOO8*、 Cr: 1
667チ。P: 0.21 excellent, S: [LOO8*, Cr: 1
667 chi.
N:α18慢の5US430鋼の拡散焼鈍し、デスケー
リング処理した161111厚の元板を第2図に示す工
程(fCだし一次冷間圧延後の処理は通常の焼鈍と酸洗
による)K従って種々の条件で最終的にα5鵡の冷延鋼
板に仕上げた。N: The original plate of 161111 thickness, which was diffusion annealed and descaled from 5US430 steel with α18 arrogance, was subjected to the process shown in Fig. 2 (fC and the treatment after the primary cold rolling was by normal annealing and pickling). Finally, α5 parrot cold-rolled steel sheet was produced under these conditions.
このようKして得られた試料冷延鋼板について。Regarding the sample cold-rolled steel sheet obtained by K in this way.
穴拡げ比とR(ランクフォード値)を調べた結果が第4
図と第5図に示されている。なお穴拡げ試験は直径10
mの元穴を切削によって穿ち1元大を球lIポンチで押
拡げ1元ycK割れが生じたときの直径dを調べ、穴拡
げ比α=(d−10)/10を求めたものである。The fourth result is the result of examining the hole expansion ratio and R (Lankford value).
As shown in FIG. The hole expansion test was performed using a diameter of 10
The diameter d at which a 1-dimensional ycK crack occurs was determined by drilling a hole of m size by cutting and expanding the 1-dimensional hole with a ball lI punch to find the hole expansion ratio α = (d-10)/10. .
第4図を見ると、−次冷関圧延の圧延率を上げ。Looking at Figure 4, we see that the rolling rate of the next cold rolling was increased.
仕上冷間圧延の圧延率を下げる程穴拡げ比が増大するこ
とがわかる。It can be seen that the hole expansion ratio increases as the rolling rate of finish cold rolling is lowered.
第9図は、−次及び仕上冷間圧延の圧延率配分とR値の
関係を調べたものである。R値は9周知の如く深絞シ性
の指標であり、引張試験片の板幅方向の対数ひずみと板
厚方向の対数ひずみの比で求められ、このR値が高い程
深絞り性が良好となるものである。第6図の結果から明
らかなようK。FIG. 9 shows an investigation of the relationship between the rolling ratio distribution and the R value in the subsequent and final cold rolling. As is well known, the R value is an index of deep drawability, and is determined by the ratio of the logarithmic strain in the sheet width direction to the logarithmic strain in the sheet thickness direction of a tensile test piece, and the higher the R value, the better the deep drawability. This is the result. As is clear from the results shown in Figure 6, K.
R値は一次冷間圧延の圧延率が約58〜80%。The R value is approximately 58 to 80% at the rolling reduction of the primary cold rolling.
仕上冷間圧延の圧延率が約57−〜約67嗟の間で、最
大値(最大のピーク領域)を取っていることが分かる。It can be seen that the maximum value (maximum peak area) is reached when the finishing cold rolling reduction is between about 57 and about 67 minutes.
つまり、深絞り性には、最大値或いは最大のピーク領域
があ)、圧延率の配合により規制され、ある圧延率の配
分領域より高くても又低くても十分な深絞り成形性は得
られないのである。In other words, deep drawability has a maximum value or a maximum peak area, and is regulated by the rolling ratio ratio, and sufficient deep drawability cannot be obtained even if the rolling ratio is higher or lower than a certain range. There isn't.
第4図と第5図の結果から、穴拡げ成形性と深絞り成形
性とを同時に満足する範囲は、R値の最大値を示す一次
冷間圧延の圧延率約58〜80%。From the results shown in FIGS. 4 and 5, the range that satisfies hole expansion formability and deep drawability at the same time is approximately 58 to 80% of the rolling ratio of the primary cold rolling that exhibits the maximum R value.
仕上冷間圧延の圧延率約37〜67哄で規制されこの範
囲に圧延率の配分をすればよい。The finishing cold rolling is regulated at a rolling rate of about 37 to 67 g, and the rolling rate may be distributed within this range.
ところが表面光沢性の方は、目視観察によって判断する
と、−次冷関圧砥の圧延率が75慢未満。However, in terms of surface gloss, as judged by visual observation, the rolling ratio of the cold grinding wheel was less than 75%.
仕上冷間圧延の圧延率が45慢以上の領域では。In the area where the finishing cold rolling reduction is 45 or higher.
前記数値の間のものよシ表m元沢変が劣るととが分かっ
た。It was found that the Motosawa variation was inferior to those between the above values.
を大表面粗度をJIS B O601r表面粗さ」測定
方法により欄定し、上記試験の代表的な試料a。The large surface roughness was determined by the JIS B O601r surface roughness measurement method, and a representative sample a of the above test.
b、eの結果を下記の表に示す。The results of b and e are shown in the table below.
次に前記の材料を、第3図に示す工程であって。Next, the above-mentioned materials are processed through the process shown in FIG.
ただし−次冷関圧砥後の処理を再結晶焼鈍醗洗に替えて
再結晶光輝焼鈍を行なうととによる工程によって、餉記
試料鳳をほぼ同一の条件によって処理した。この試料d
Kついての結果も上記の表に記3れている。However, the process after cold grinding was replaced with recrystallization annealing and recrystallization bright annealing. This sample d
The results for K are also listed in the table above.
一方同じ材料を第74’2図に示す工程(−次冷間圧延
後焼鈍醗洗による)によって試料aとほぼ同様に処理し
た試料6は本発明方法による試料aと略々同様の結果を
示した。なおこの試料作製の軽研摩はポリビニルアルコ
ールをバインダーとする参1000砥材を用いて行なっ
た。On the other hand, sample 6, which was made of the same material and processed in the same manner as sample a by the process shown in FIG. Ta. Note that light polishing for preparing this sample was performed using a No. 1000 abrasive material containing polyvinyl alcohol as a binder.
ここに見られるように第;t’l’2図に示す従来方法
による試料e(製品)は本発明の方法の試料a及びd(
製品)と略同勢の品質を示すことが判明する。一方、従
来方法による試料す及びC(製品)は9本発明試料a及
びd(製品)K比較して一次冷関圧延率が低く反対に仕
上冷間圧延率が高いため、R値に差は認められないもの
の穴拡げ比ゆは低く、且つ表面粗度が大で表面光沢が悪
い。As seen here, sample e (product) obtained by the conventional method shown in Fig.
It turns out that the quality is almost the same as that of the product). On the other hand, samples A and C (products) made by the conventional method have a lower primary cold rolling rate and a higher finishing cold rolling rate compared to 9 inventive samples a and d (products) K, so there is no difference in R value. Although it is not recognized, the hole expansion ratio is low, the surface roughness is high, and the surface gloss is poor.
以上記し穴ように本願発明の産業上の効用は極めて大と
いわねばならぬ。As mentioned above, it must be said that the industrial utility of the present invention is extremely large.
第r/1.I’72図は従来方法の工程を示す流れ図で
ある。
第3図は本発明方法の工程を示す流れ図である。
第4図は冷間圧延ステンレス鋼板の冷間圧延における一
久圧延率と仕上圧延率とランクフォード(R)値の関係
を示すグラフである。
第5図は冷間圧延ステンレス鋼板の冷間圧延における一
久圧延軍と仕上圧延率と冗拡げ比ゆの関係を示すグラフ
である。
特許出願人 日新製鋼株式会社
代理人 弁理士 松 井 政 広(外2名)第5因
F−i+<φ)
特許庁長官 島 1)春樹殿
1、事件の表示
昭和56 年特 許 願第120632号 。
3 補正をする者
事件との関係 特許出願人
住 所
氏 名銘称)(458) 日新製鋼株式会社4代理人
5、補正命令の日付自発
6、 補正により増加する発明の数 なし記正誤表に示
した各頁・行における「補正前(誤)」の記載を、「補
正後(正)」のように訂正する。
41B 第2図 第6図
5 6 硬式ロール 硬質ロール520 研
磨 研摩
7 7 (この方が・−といわ (削除)れている)
162 第2図 第6図
18 4 流れ図 工程図18 6 流
れ図 工程図18 8−次圧延率と仕上
−次圧延率および圧延率 仕上圧
幌率
188〜9ランクフォード(R)値 穴拡げ比(α)
1811−次圧延率と仕上 −矢玉4i−率および
圧延率 仕上圧延率
1811穴拡は比(α) ランクフォーr
(R)値■ 同第13頁15行目と16行目の間に下記
の一節を挿入する。
[ここで顧客側での加工で要求される穴拡げ比(ψは、
顧客側の加工内容により差があるが、特別に穴拡げ成形
性を要求される場合、穴拡げ比(ψで概ね0.75以上
である。従って第4図の結果から穴拡げ成形性はバラツ
キ本考慮すると一次冷間圧延の圧延率が約75チ以上、
仕上冷関圧延の圧延率が約44ts以下で良好なものが
得られる。」璽 同第14頁10行目から20行目、第
15頁全行および第17頁全行を削除し、下記の一節を
挿入する。
致する一次冷間圧延の圧延率約75〜80%、仕上冷間
圧延の圧延率約67〜44嘩で規制されるこの範囲に圧
延率の配分をすればよい。
ところが表面光沢性の方は下記の表に示す5U8430
の加工結果で、目視観察によって判断すると従来法の第
1図の工場により処理した試料す。
eFit %々表面党沢寂が中・下のランクに判定され
、−次冷関圧延軍の圧延率が高く、仕上冷関圧延の圧延
率が低い方が悪くなっている。
しかしながら1本発明の第5図の工程でおって一次冷間
圧延後の処理を再結晶焼鈍・酸洗で処理した試料aは、
上記試料Cよりさらに一次冷関圧延の圧延率が高く、仕
上冷間圧延の圧延率が低いにもかかわらず表面光沢度が
上のランクに判定されている。
この表面光沢性を定量的に判断する為に表面粗度をJI
8 BO601r表面粗さ」測定方法により測定し比較
してみると、従来法の第1図の工程により処理した試料
すが02〜0.3μ、試料Cが0,6〜0.4μに対し
9本発明の第3WJの工程により処理した試料aは0.
1〜α2μと上記表面粗度の判定とつき合わせてみると
表面粗度が小さいもの程表面光沢が優れてお抄同じ傾向
を示している。
一方大波げ比(ψ及びR値については本発明の第3図の
工程で処理すると、従来法の第1図の工程で処理したも
のと、R値には差は認められないものの、大波げ比(α
)は低く優れているといえる。
また1本発明の試料aは比較的最近の直前従来技術の第
2図の工程で処理し九試料・とほぼ同等の表面光沢度゛
・表面粗度・大波は比((資)・R値であるので本発明
は比較的最近の直前従来技術の第2図の工程で処理する
方法にとって代ることができると判断する。
なお、第3図の工程で一次冷間圧延後の再結晶焼鈍―實
洗の代りに、再結晶光輝焼鈍で処理した試料dも示すが
試料aと何ら変りがないので一次冷間圧延後の再結晶焼
鈍処理はどちらの方法で行なってもよいといえる。j
■ 同第16頁の表を下肥のように訂正する。
■ 図面の第150および第2図を添付図面のように訂
正する。No. r/1. Figure I'72 is a flowchart showing the steps of the conventional method. FIG. 3 is a flowchart showing the steps of the method of the present invention. FIG. 4 is a graph showing the relationship between the rolling rate, finishing rolling rate, and Lankford (R) value in cold rolling of a cold rolled stainless steel sheet. FIG. 5 is a graph showing the relationship between the first rolling force, the finishing rolling rate, and the redundancy expansion ratio in cold rolling of a cold rolled stainless steel plate. Patent Applicant Nisshin Steel Co., Ltd. Agent Patent Attorney Masahiro Matsui (2 others) Fifth Factor F-i+<φ) Commissioner of the Japan Patent Office Shima 1) Haruki-dono 1, Indication of Case 1982 Patent Application No. No. 120632. 3 Relationship with the case of the person making the amendment Patent applicant address Name) (458) Nisshin Steel Co., Ltd. 4 Agent 5 Date of amendment order Voluntary 6 Number of inventions increased by amendment Errata with no blank On each page and line shown in , the description "Before amendment (incorrect)" will be corrected as "After amendment (correct)." 41B Fig. 2 Fig. 6 Fig. 5 6 Hard roll Hard roll 520 Polishing Polishing 7 7 (This one has been deleted) 162 Fig. 2 Fig. 6 Fig. 18 4 Flow diagram Process diagram 18 6 Flow diagram Process diagram 18 8 - Next rolling rate and finishing - Next rolling rate and rolling rate Finishing rolling rate 188-9 Lankford (R) value Hole expansion ratio (α)
1811-Next rolling rate and finishing - Arrow ball 4i-rate and rolling rate Finishing rolling rate 1811 hole expansion ratio (α) Rank four r
(R) Value■ Insert the following passage between lines 15 and 16 on page 13. [Here, the hole expansion ratio (ψ) required by the customer's processing is
There are differences depending on the customer's processing details, but if special hole expansion formability is required, the hole expansion ratio (ψ) should be approximately 0.75 or more. Therefore, the results shown in Figure 4 show that hole expansion formability varies. Considering this, the rolling ratio of primary cold rolling is about 75 inches or more,
A good product can be obtained when the rolling rate of the final cold rolling is about 44 ts or less. ” Seal Delete lines 10 to 20 on page 14, all lines on page 15, and all lines on page 17, and insert the following passage. The rolling ratio may be distributed within this range, which is regulated by the rolling ratio of about 75 to 80% for the primary cold rolling and about 67 to 44% for the finishing cold rolling. However, for surface gloss, 5U8430 shown in the table below
Judging from visual observation, the processing results show that the sample was processed using the conventional method at the factory shown in Figure 1. eFit % Tozawa Jaku on the surface is judged to be in the middle/lower rank, the rolling rate of the second cold rolling group is high, and the rolling rate of the finishing cold rolling is low. However, sample a, which was processed by recrystallization annealing and pickling after the primary cold rolling in the process shown in FIG. 5 of the present invention,
Even though the rolling rate in the primary cold rolling was higher than that of Sample C, and the rolling rate in the finishing cold rolling was lower, the surface glossiness was ranked higher. In order to quantitatively judge this surface glossiness, the surface roughness is determined by JI.
8 BO601r surface roughness" measurement method and compared, it was found that the sample treated by the process shown in Figure 1 of the conventional method had a roughness of 0.2 to 0.3μ, and sample C had a roughness of 0.6 to 0.4μ, while sample C had a roughness of 9. Sample a treated by the third WJ process of the present invention was 0.
Comparing 1 to α2μ with the surface roughness determination described above, the smaller the surface roughness, the better the surface gloss, showing the same tendency as papermaking. On the other hand, regarding the large wave ratio (ψ and R value), when processed using the process shown in Figure 3 of the present invention, there is no difference in R value compared to that processed using the process shown in Figure 1 of the conventional method. Ratio (α
) can be said to be low and excellent. In addition, sample a of the present invention was processed using the process shown in FIG. Therefore, it is judged that the present invention can replace the relatively recent prior art method of processing in the process shown in Fig. 2.In addition, in the process shown in Fig. 3, recrystallization annealing after primary cold rolling is performed. - Sample d, which was treated with recrystallization bright annealing instead of actual washing, is also shown, but since it is no different from sample a, it can be said that either method can be used for recrystallization annealing after primary cold rolling.j ■ Correct the table on page 16 of the same page to read "lower manure." ■ Correct figures 150 and 2 of the drawings to read as shown in the attached drawing.
Claims (1)
をデスケーリング処理し、粗研摩し、75〜80憾の圧
延率で一次冷間圧延を施し、再結晶焼鈍・酸洗し、無潤
滑調質圧延を行ない、圧延率57〜44嘔の仕上冷間圧
延を行ない、再結晶光輝焼鈍を行ない、最後に無潤滑調
質圧延を行なうことからなる成形性と表面光沢性に優れ
たフェライト系ステンレス鋼検電鋼板の製造法。 2、%許請求範@l第1項に記載の方法であって。 最初の無潤滑調質圧延の圧延率がα5〜S、OSであシ
、最後の無潤滑調質圧延の圧延率が0.8〜t2慢であ
ることを特徴とする方法。 五 拡散焼鈍を施しであるかまたは施してない熱延鋼帯
を、デスケーリング処理し、粗研摩し。 75〜80嘔の圧延率で一次冷間圧延を施し、再結晶光
輝焼鈍を行ない、無潤滑調質圧延を行ない。 圧延率57〜4496の仕上冷間圧延を行ない、再結晶
光輝焼鈍を行ない、最後に無潤滑調質圧延を4、%許請
求の範囲第3項に記載の方法であって。 最初の無潤滑調質圧延の圧延率がQ、5〜50%であり
、最後の無潤滑調質圧延の圧延率がα8〜12%である
ことを!像とする方法。[Scope of Claims] 1. A hot-rolled steel strip that has been subjected to diffusion annealing or has not been subjected to overlapping is descaled, roughly polished, and subjected to primary cold rolling at a rolling ratio of 75 to 80, and then recrystallized. Formability, which consists of annealing and pickling, non-lubricated temper rolling, final cold rolling at a rolling reduction of 57 to 44 mm, recrystallization bright annealing, and finally non-lubricated temper rolling. A method for manufacturing ferritic stainless steel electrical testing steel plates with excellent surface gloss. 2. The method according to claim 1. A method characterized in that the rolling rate of the first non-lubricated skin pass rolling is α5 to S, OS, and the rolling rate of the final non-lubricated skin pass rolling is 0.8 to t2. 5. Descaling and rough polishing the hot rolled steel strip, which may or may not have been diffusion annealed. Primary cold rolling is performed at a rolling ratio of 75 to 80 mm, recrystallization bright annealing is performed, and non-lubricated temper rolling is performed. The method according to claim 3, wherein finish cold rolling is performed at a rolling reduction of 57 to 4496, recrystallization bright annealing is performed, and finally non-lubricated skin pass rolling is performed at a rolling rate of 4.%. The rolling ratio of the first non-lubricated skin pass rolling is Q, 5 to 50%, and the rolling ratio of the last non-lubricated skin pass rolling is α8 to 12%! How to make it into a statue.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP12063281A JPS5822330A (en) | 1981-08-03 | 1981-08-03 | Production of cold-rolled ferritic stainless steel sheet excellent in formability and surface brightness |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP12063281A JPS5822330A (en) | 1981-08-03 | 1981-08-03 | Production of cold-rolled ferritic stainless steel sheet excellent in formability and surface brightness |
Publications (1)
Publication Number | Publication Date |
---|---|
JPS5822330A true JPS5822330A (en) | 1983-02-09 |
Family
ID=14791022
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP12063281A Pending JPS5822330A (en) | 1981-08-03 | 1981-08-03 | Production of cold-rolled ferritic stainless steel sheet excellent in formability and surface brightness |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS5822330A (en) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0375384A2 (en) * | 1988-12-23 | 1990-06-27 | Kawasaki Steel Corporation | Method and apparatus for pre-processing stainless steel strip intended to be cold-rolled |
JP2002532254A (en) * | 1998-12-18 | 2002-10-02 | アヴェスタ シェフィールド アクツィアブーラーグ (ペーユーベーエル) | Strip manufacturing method and rolling mill line |
-
1981
- 1981-08-03 JP JP12063281A patent/JPS5822330A/en active Pending
Cited By (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP0375384A2 (en) * | 1988-12-23 | 1990-06-27 | Kawasaki Steel Corporation | Method and apparatus for pre-processing stainless steel strip intended to be cold-rolled |
EP0375384A3 (en) * | 1988-12-23 | 1992-01-15 | Kawasaki Steel Corporation | Method and apparatus for pre-processing stainless steel strip intended to be cold-rolled |
JP2002532254A (en) * | 1998-12-18 | 2002-10-02 | アヴェスタ シェフィールド アクツィアブーラーグ (ペーユーベーエル) | Strip manufacturing method and rolling mill line |
EP1637243A3 (en) * | 1998-12-18 | 2006-08-09 | Outokumpu Stainless AB | Method for manufacturing of stainless steel strips and rolling mill line |
JP4759698B2 (en) * | 1998-12-18 | 2011-08-31 | ユートキュムプ オサケ ユキチュア ユルキネン | Strip manufacturing method and rolling mill line |
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