JPS63166931A - Manufacture of high tension hot rolled steel sheet having high magnetic flux density - Google Patents
Manufacture of high tension hot rolled steel sheet having high magnetic flux densityInfo
- Publication number
- JPS63166931A JPS63166931A JP61315806A JP31580686A JPS63166931A JP S63166931 A JPS63166931 A JP S63166931A JP 61315806 A JP61315806 A JP 61315806A JP 31580686 A JP31580686 A JP 31580686A JP S63166931 A JPS63166931 A JP S63166931A
- Authority
- JP
- Japan
- Prior art keywords
- magnetic flux
- flux density
- steel sheet
- strength
- rolled steel
- 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
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 43
- 239000010959 steel Substances 0.000 title claims abstract description 43
- 230000004907 flux Effects 0.000 title claims abstract description 21
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 8
- 238000001816 cooling Methods 0.000 claims abstract description 20
- 238000005098 hot rolling Methods 0.000 claims abstract description 11
- 230000009466 transformation Effects 0.000 claims abstract description 9
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 6
- 229910052742 iron Inorganic materials 0.000 claims abstract description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 4
- 238000010438 heat treatment Methods 0.000 claims description 6
- 238000004804 winding Methods 0.000 claims description 4
- 229910052799 carbon Inorganic materials 0.000 abstract description 3
- 230000000694 effects Effects 0.000 description 9
- 238000005728 strengthening Methods 0.000 description 9
- 239000013078 crystal Substances 0.000 description 8
- 230000005415 magnetization Effects 0.000 description 6
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 238000001556 precipitation Methods 0.000 description 5
- 239000000126 substance Substances 0.000 description 5
- 238000000034 method Methods 0.000 description 4
- 230000006866 deterioration Effects 0.000 description 3
- 230000003014 reinforcing effect Effects 0.000 description 3
- 239000006104 solid solution Substances 0.000 description 3
- 230000002542 deteriorative effect Effects 0.000 description 2
- 230000005381 magnetic domain Effects 0.000 description 2
- 238000010248 power generation Methods 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 238000005275 alloying Methods 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000005611 electricity Effects 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000035699 permeability Effects 0.000 description 1
- 239000003208 petroleum Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000002966 varnish Substances 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
- C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
- C21D8/1222—Hot rolling
Landscapes
- Engineering & Computer Science (AREA)
- Chemical & Material Sciences (AREA)
- Physics & Mathematics (AREA)
- Electromagnetism (AREA)
- Manufacturing & Machinery (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacturing Of Steel Electrode Plates (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は高磁束密度を有する高張力熱延鋼板の製造方法
に係り、特に近時発電機の高性能化に即応せしめ降伏点
８Ｑｋｇ／ｍｍ”以上、引張強さ１００ｋｇ ／ ｗ
２以上の磁極用高強度熱延鋼板に好適な高張力熱延鋼板
の製造方法に関するものである。Detailed Description of the Invention (Industrial Application Field) The present invention relates to a method for manufacturing a high-strength hot-rolled steel sheet having a high magnetic flux density, and particularly to a method for producing a high-strength hot-rolled steel sheet having a yield point of 8 Q kg/mm, which is particularly suitable for the recent high performance of power generators. ” or more, tensile strength 100kg/w
The present invention relates to a method for manufacturing a high-strength hot-rolled steel sheet suitable for use as a high-strength hot-rolled steel sheet for two or more magnetic poles.
（従来の技術）
近年における石油危機に端を発して世界的に脱石油エネ
ルギーの傾向が強まっているが、電力についても水力発
電が見立される傾向にある。これに伴っｔ発電能力の向
上が要求されるようになり、発電機の高回転、高出力化
が進められており、このような背景のものに回転子の一
部であるローターリムやポールピースに使用される鋼板
についてもより強度の高いものが必要とされるようにな
った。(Prior Art) The recent oil crisis has led to a worldwide trend toward a shift away from petroleum energy, and there is also a trend toward hydroelectric power generation as a source of electricity. Along with this, there has been a demand for improved power generation capacity, and generators are being made to have higher rotation speeds and higher outputs. Steel plates with higher strength are now required for use in automobiles.
従来引張強さ８０ｋｇ／１ｍ”以上の高強度熱延鋼板は
主に自動車、建設機械に用いられる冷間での加工性が良
好であるものが検討されており、以下の特許文献に示さ
れる物がある。Conventionally, high-strength hot-rolled steel sheets with a tensile strength of 80 kg/1 m'' or more have been considered that have good cold workability and are mainly used in automobiles and construction machinery, and the ones shown in the following patent documents are There is.
特公昭５３−４３８８４号公報、特公昭５４−１４０４
６号公報。Special Publication No. 53-43884, Special Publication No. 54-1404
Publication No. 6.
特公昭５８−２１０１０号公報、特開昭５３−８８６２
０号公報。Japanese Patent Publication No. 58-21010, Japanese Patent Publication No. 53-8862
Publication No. 0.
特開昭５９−１６３２号公報、特開昭５９−１５００１
８号公報
しかし、これらはいずれも冷間での加工性が良好である
ことを狙ったもので、本発明のように磁束密度と強度を
合わせ持つことを狙ったものではない。JP-A-59-1632, JP-A-59-15001
Publication No. 8 However, all of these are aimed at having good cold workability, and are not aimed at having both magnetic flux density and strength like the present invention.
一方、高磁束密度を有する高強度熱延鋼板として特開昭
５８−９１１２１号公報に示されているようなものがあ
るが、その強度レベルは降伏点８０ｋｇ／１ｍ”以下、
引張強さ１００ｋｇ／ｎ＋”以下のもので、上記したよ
うな発電機の高性能化に伴い高速回転でも磁極を保持で
きるように降伏点、引張強さの何れもがより高いものを
満足するものではない。On the other hand, there is a high-strength hot-rolled steel sheet with a high magnetic flux density, such as that shown in Japanese Patent Application Laid-Open No. 58-91121, but its strength level is below the yield point of 80 kg/1 m'',
A material with a tensile strength of 100 kg/n+" or less, which satisfies both the yield point and tensile strength to be higher so that the magnetic pole can be maintained even at high speed rotation as the performance of generators increases as mentioned above. isn't it.
また、特公昭６１−１１２８８号公報では降伏点７０〜
１１０ｋｇ／鶴茸、引張強さ８０〜１２０ｋｇ／鶴２の
ものが提案されている。しかし、この方法は熱延鋼板の
形状および強靭性の観点からのみ検討されていて、要求
される磁束密度についてはなんら考慮されていない。In addition, in Japanese Patent Publication No. 61-11288, the yield point is 70~
One with a tensile strength of 110 kg/Tsurutake and a tensile strength of 80 to 120 kg/Tsuru2 has been proposed. However, this method has been studied only from the viewpoint of the shape and toughness of the hot rolled steel sheet, and no consideration has been given to the required magnetic flux density.
（発明が解決しようとする問題点）
本発明は、降伏点８０ｋｇ／鶴”以上、引張強さ１００
ｋｇ／ ｗ”以上、磁束密度Ｂ１＋ｏ１．７Ｔｅｓｌ
ａ以上を有する高強度熱延鋼板を的確に製造し得る新し
い方法を提供することを目的とする。(Problems to be Solved by the Invention) The present invention has a yield point of 80 kg/Tsuru” or more and a tensile strength of 100
kg/w” or more, magnetic flux density B1+o1.7Tesl
It is an object of the present invention to provide a new method that can accurately produce a high-strength hot-rolled steel sheet having a strength of at least a.
（問題点を解決するための手段）
本発明の要旨とするところは、重量比にてＣ；０．０５
〜０．１５％、Ｓｉ：０．５０％以下、Ｍｎ ： ０．
７０〜２．００％、Ｐ ： ０．０２０％以下、Ｓ ：
０．０１０％以下、ｓ’ｏｌ Ａｊ ；０．０１０〜
０．１０％、Ｎ ： ０．００５０％以下、Ｔｉ：０．
１０〜０６３０％、Ｂ：０．００１５〜０．００５０％
を含み、残部はＦｅおよび不可避的不純物より成る鋼ス
ラブを、加熱温度１２００℃以上に加熱し、熱延仕上温
度Ａｒ、変態点以上９５０℃以下で熱間圧延し、冷却速
度３０℃／ｓｅｃ以上７０℃／ｓｅｃ未満で冷却し、５
００℃以下で巻取ることを特徴とする高磁束密度を有す
る高張力熱延鋼板の製造方法にある。(Means for Solving the Problems) The gist of the present invention is that the weight ratio of C; 0.05
~0.15%, Si: 0.50% or less, Mn: 0.
70-2.00%, P: 0.020% or less, S:
0.010% or less, s'ol Aj; 0.010~
0.10%, N: 0.0050% or less, Ti: 0.
10-0630%, B: 0.0015-0.0050%
A steel slab containing Fe and the remainder consisting of Fe and unavoidable impurities is heated to a heating temperature of 1200°C or higher, hot-rolled at a hot-rolling finishing temperature Ar, above the transformation point and below 950°C, and at a cooling rate of 30°C/sec or above. Cool at less than 70°C/sec,
The present invention provides a method for producing a high-tensile hot-rolled steel sheet having a high magnetic flux density, which is characterized by winding at a temperature of 00°C or lower.
以下、本発明の詳細について説明する。The details of the present invention will be explained below.
本発明の目的である高磁束密度を得るためには鋼中の不
純物を減少して純鉄に近付けるのが効果的であることは
公知であるが、それでは高強度を確保し得ない０本発明
のように降伏点８０１ｑｒ／ｎ＋”以上、引張強さ１０
０ ｋｇ／ｖａ”以上の高強度熱延鋼板を得るには固溶
体強化だけでは無理で、析出強化あるいは変態組織強化
をも組あわせる必要がある。これらの強化機構を磁束密
度を劣化させないで使うことが本発明の主旨である。It is well known that it is effective to reduce impurities in steel to make it closer to pure iron in order to obtain a high magnetic flux density, which is the objective of the present invention, but this does not ensure high strength. Yield point 801qr/n+" or higher, tensile strength 10
In order to obtain high-strength hot-rolled steel sheets with a strength of 0 kg/va" or higher, solid solution strengthening alone is not possible, and it is necessary to combine precipitation strengthening or transformation structure strengthening. These strengthening mechanisms must be used without deteriorating the magnetic flux density. This is the gist of the present invention.
不純物のうちで最も磁束密度に悪影響を及ぼすのはＣ，
Ｎ等の侵入型原子である。これらはＦｅの結晶格子内に
侵入して格子ひずみを増大させ、磁区の移動を妨げる＊
Ｓｔ＋ Ｍｎの置換型原子も結晶格子を歪ませるがＣ
，Ｎ等の侵入型原子よりもその影響は少ない。一方、析
出強化元素として知られるＴｔ、 Ｎｂ＋ Ｖ、 Ｚｒ
は微細炭化物もしくは窒化物として鋼中に析出し転位の
移動を妨げ鋼を強化するが、磁区の移動は妨げないと考
えられている。これらの元素はＣを炭化物として固定し
鋼を強化するので本発明の目的に効果的である。特にＴ
ｉは安価であって、かつ少量で強度を向上でき、しかも
Ｎを固定するので磁束密度を高くし、かつ焼き入れ性の
向上を狙って添加するＢが有効に作用するので、極めて
有効な元素である。即ち、第１図、第２図に示されるよ
うにＢが添加され、熱間圧延後のランナウトテーブル上
の冷却速度が速いと磁束密度を低下させる合金元素を大
量に添加せずに有効に強化することが可能である。Among the impurities, C has the most negative effect on magnetic flux density.
These are interstitial atoms such as N. These penetrate into the crystal lattice of Fe, increase lattice strain, and impede movement of magnetic domains*
Substituted atoms of St+ Mn also distort the crystal lattice, but C
The effect is less than that of interstitial atoms such as , N, etc. On the other hand, Tt, Nb+V, Zr, which are known as precipitation strengthening elements
It is thought that they precipitate in steel as fine carbides or nitrides and strengthen the steel by hindering the movement of dislocations, but do not impede the movement of magnetic domains. These elements are effective for the purpose of the present invention because they fix C as carbide and strengthen the steel. Especially T
i is an extremely effective element because it is inexpensive, can improve strength with a small amount, and fixes N to increase magnetic flux density, and B, which is added to improve hardenability, works effectively. It is. That is, as shown in Figures 1 and 2, when B is added and the cooling rate on the runout table after hot rolling is fast, it is effectively strengthened without adding large amounts of alloying elements that reduce magnetic flux density. It is possible to do so.
本発明における上記鋼成分の限定理由は次の如くである
。The reasons for limiting the above-mentioned steel components in the present invention are as follows.
Ｃ：
Ｃは高い引張強さを得るために最も効果的な元素であっ
て、この目的のために少なくとも０．０５％を必要とす
る。しかし、Ｃの増加と共に磁化特性が劣化するので、
その上限を０．１５％とし、０．０５〜０．１５％の範
囲に限定した。C: C is the most effective element for obtaining high tensile strength and requires at least 0.05% for this purpose. However, as the magnetization characteristics deteriorate as C increases,
The upper limit was set to 0.15%, and the range was limited to 0.05 to 0.15%.
Ｓｉ：
Ｓｉは強化元素として有用であるが、磁化特性を劣化さ
せるので少ない方が望ましい。しかし、強化元素として
最小限の添加によって鋼を経済的に製造するために０．
５０％を上限として添加することとした。Si: Si is useful as a reinforcing element, but it degrades the magnetization properties, so it is desirable to have a small amount. However, in order to economically produce steel with minimal addition of reinforcing elements, 0.
It was decided to add up to 50%.
Ｍｎ：
Ｍｎも強度の向上には効果的な元素であるが、磁化特性
を劣化させる。しかし、Ｓｉに比較すると劣化程度は小
さい。そのため強化元素として少なくとも０．７０％を
必要とする。しかし、２．００％を越すと磁化特性の劣
化が大となるので上限を２．００％とし、０．７０〜２
．００％の範囲に限定した。Mn: Mn is also an effective element for improving strength, but it deteriorates magnetization characteristics. However, compared to Si, the degree of deterioration is small. Therefore, at least 0.70% of the reinforcing element is required. However, if it exceeds 2.00%, the deterioration of the magnetization characteristics will be significant, so the upper limit is set at 2.00%, and 0.70 to 2.
．． 00% range.
５ｏＺＡｆ：
５ｏｌｋｌは脱酸上０．０１０％以上必要であるが、０
．１０％を越すと結晶粒の粗大化を来たし強度を劣化さ
せると共に磁化特性の劣化も大となるので０．１０％以
下に限定した。5oZAf: 5olkl is required for deoxidation at 0.010% or more, but 0
．． If it exceeds 10%, the crystal grains become coarse and the strength deteriorates, and the magnetization characteristics also deteriorate significantly, so it is limited to 0.10% or less.
Ｐ、Ｓ：
Ｐ、Ｓは何れも不純物元素であって、鋼の延性や靭性を
害するので少ないほど好ましいものでＰは０．０２０％
以下、Ｓは０．０１０％以下にする必要がある。P, S: Both P and S are impurity elements, and since they impair the ductility and toughness of steel, it is preferable to have as little as possible, and P is 0.020%.
Hereinafter, S needs to be 0.010% or less.
Ｎ ：
Ｎは侵入型原子として結晶格子を歪ませ磁化特性を劣化
させるほか、本発明でとくに添加したＢと結合してＢＮ
を形成して、焼き入れ性向上に対し有効に作用しなくな
る。この防止策としてＴｉを添加するのであるが、Ｎが
多量にあるとＢＮを形成し焼き入れ性向上効果を減少さ
せてしまうので上限を０．００５０％に限定した。N: N acts as an interstitial atom, distorting the crystal lattice and deteriorating the magnetization properties, and also combines with B, which is especially added in the present invention, to form BN.
is formed, and the hardenability is no longer effectively improved. To prevent this, Ti is added, but if a large amount of N is present, BN will be formed and the effect of improving hardenability will be reduced, so the upper limit was limited to 0.0050%.
Ｔｉ：
Ｔｉは安価で、しかも少量の添加によってＣと結合して
ＴｉＣを形成し鋼を強化するので少なくとも０．１０％
を必要とする。Ｔｉが多くなると表面疵の原因になるの
で上限を０．３０％とした。Ti: Ti is inexpensive, and when added in small amounts, it combines with C to form TiC and strengthens steel, so it should be at least 0.10%.
Requires. If Ti increases, it causes surface flaws, so the upper limit was set at 0.30%.
Ｂ：
Ｂは熱間圧延終了後の冷却速度が３０°Ｃ／ｓｅｃ以上
の急冷下において焼き入れ性を向上させ、ヘイナイト組
織を得やすくする作用があるが、０．００１５％未満で
は前記作用に所望の効果が得られず、一方０．００５０
％を超えて含有させてもその効果が飽和してしまうこと
から、その含有量を０．００１５〜ｏ、 ｏ ｏ ｓ
ｏ％に限定した。B: B improves hardenability under rapid cooling at a cooling rate of 30°C/sec or more after hot rolling, and has the effect of making it easier to obtain a haynite structure, but if it is less than 0.0015%, the above effect is impaired. The desired effect was not obtained, while 0.0050
Since the effect will be saturated even if the content exceeds 0.0015 to 0.0015 o, o o s
o%.
熱延条件ニ
スラブの加熱は一度冷片としたもの、もしくは熱片のま
まのものも１２００℃以上に加熱する。通常１２００℃
〜１４００℃の温度範囲に加熱した後圧延する。Hot rolling conditions The varnish slab is heated to 1200° C. or higher once it has been turned into a cold piece, or even if it is still a hot piece. Normally 1200℃
It is heated to a temperature range of ~1400°C and then rolled.
加熱温度を１２００℃以上としたのはＴｉの固溶を促進
するためであって１２００℃未満の加熱温度ではＴｉが
十分固溶されないからである。上限は特に限定しないが
、スケールロスの防止、省エネルギーの観点から１４０
０℃を越す加熱は不必要である。The reason why the heating temperature is set to 1200° C. or higher is to promote solid solution of Ti, and this is because Ti is not sufficiently dissolved at a heating temperature of less than 1200° C. The upper limit is not particularly limited, but from the perspective of preventing scale loss and saving energy, it is 140
Heating above 0°C is unnecessary.
上記１２００℃以上に加熱したスラブを熱延圧延し、そ
の仕上温度をＡｒ３変態点以上としたのは、ＴｉＣの析
出による強度確保と残留歪による透磁率劣化を防止する
ためであって、Ａｒ３変態点未満の仕上圧延温度ではこ
の目的が達成されないからである。The reason why the slab heated above 1200°C was hot-rolled and the finishing temperature was set at above the Ar3 transformation point was to ensure strength due to TiC precipitation and to prevent magnetic permeability deterioration due to residual strain. This is because this objective cannot be achieved if the finish rolling temperature is below this point.
また、９５０℃を越す仕上圧延温度では高温過ぎて鋼板
の結晶粒が粗大化し、必要な強度が得られない。Further, if the finish rolling temperature exceeds 950°C, the temperature is too high and the crystal grains of the steel sheet become coarse, making it impossible to obtain the necessary strength.
冷却・巻取条件：
熱間圧延終了してからの冷却速度は成分とともに鋼板の
組織制御に不可欠の条件である。引張強さ１００ｋｇ／
ｆ１２以上の高強度熱延鋼板を得るには固溶体強化だけ
では無理で、析出強化あるいは変態組織強化をも組あわ
せる必要があり、冷却制御によって微細なフェライト組
織を狙う。冷却速度が３０℃／ｓｅｅ以下ではフェライ
ト）Ｊｌ織が粗大化して必要な強度が得られない。また
、引張強さ１００ ｋｇ／ｍｍ２（７）高強度ｔ！ｉＪ
［ｊテも伸びハフ ％以上必要であるが、冷却速度が７
０℃／ｓｅｃ以上ではマルテンサイト組織になり伸びが
低下して使用目的にあわない。Cooling and coiling conditions: The cooling rate after hot rolling is an essential condition for controlling the structure of the steel sheet, as well as the composition. Tensile strength 100kg/
In order to obtain high-strength hot-rolled steel sheets with f12 or higher, solid solution strengthening alone is not possible; it is necessary to combine precipitation strengthening or transformation structure strengthening, and a fine ferrite structure is aimed at through cooling control. If the cooling rate is less than 30° C./see, the ferrite (Jl) weave becomes coarse and the necessary strength cannot be obtained. In addition, the tensile strength is 100 kg/mm2 (7) high strength t! iJ
[j Te also requires elongation huffing % or more, but if the cooling rate is 7
If it exceeds 0° C./sec, it becomes a martensitic structure and elongation decreases, which is not suitable for the purpose of use.
巻取温度が高いと変態が完了しないうちに巻き取られ、
巻取後の保温中に変態するので結晶粒が粗大化し、目的
の強度が得られないので、５００℃以下と限定した。If the winding temperature is high, it will be rolled up before the transformation is completed,
The temperature was limited to 500° C. or lower because the crystal grains would become coarse due to transformation during heat retention after winding and the desired strength could not be obtained.
かくの如き製造方法によって磁束密度の高い高張力熱延
鋼板を得ることが出来る。A high tensile strength hot rolled steel sheet with a high magnetic flux density can be obtained by such a manufacturing method.
（実施例）
第１表に示される化学成分組成の鋼を転炉で溶製し、連
続鋳造により鋳片とした。化学成分についてみると、Ａ
、Ｂ、Ｃ，Ｄ鋼は本発明の要旨を満足するものである。(Example) Steel having the chemical composition shown in Table 1 was melted in a converter and made into slabs by continuous casting. Looking at the chemical components, A
, B, C, and D steels satisfy the gist of the present invention.
Ｅ、Ｆ、Ｇ鋼は比較のためのものである。第２表に熱間
圧延条件とそのとき得られた鋼板の機械的性質および磁
束密度が示されている。これによると、鋼板１１ｍ１〜
５は本発明の要旨を満足するものである。しかし、隘６
は化学成分は満足しているが熱間圧延後の冷却速度が遅
く結晶粒が大きく目的の強度が得られていない。E, F, and G steels are for comparison. Table 2 shows the hot rolling conditions and the mechanical properties and magnetic flux density of the steel sheets obtained. According to this, steel plate 11m1 ~
No. 5 satisfies the gist of the present invention. However, 6th
Although the chemical composition is satisfactory, the cooling rate after hot rolling is slow and the crystal grains are large, making it impossible to obtain the desired strength.
また、患７も化学成分は満足しているが巻取温度が高く
結晶粒が大きく目的の強度が得られていない。ＮＩＩＬ
８は強度は満足しているが０％が高く目的の磁束密度が
得られていない。Ｎａ９．Ｎａ１ＯはＢの添加量が少な
いために変態組織強化がなされず、隘１１はＴｉの添加
量が少ないため析出強化がおこなわれず、いずれも目的
の強度が得られていない。In addition, although the chemical composition of sample No. 7 is satisfactory, the coiling temperature is high and the crystal grains are large, making it impossible to obtain the desired strength. NIIL
No. 8 has satisfactory strength, but 0% is high and the desired magnetic flux density cannot be obtained. Na9. In Na1O, the transformation structure was not strengthened because the amount of B added was small, and in No. 11, precipitation strengthening was not performed because the amount of Ti added was small, and the desired strength was not obtained in either case.
第１図はＡ鋼およびＦ鋼について冷却速度と引張試験値
との関係が示されており、これによると強度を高めるた
めにはＢ添加と冷却速度を速くすることが有効であるこ
とが判る。このように、ｈ＋Ｂを適量添加し、０％は出
来るだけ低くした化学成分の鋼を冷却速度を速くするこ
とによって、磁束密度の高い高張力熱延鋼板を得ること
が出来る。Figure 1 shows the relationship between cooling rate and tensile test value for A steel and F steel, and it shows that adding B and increasing the cooling rate are effective in increasing strength. . In this way, by adding an appropriate amount of h+B and increasing the cooling rate of steel whose chemical composition is as low as possible with 0%, a high-tensile hot-rolled steel sheet with a high magnetic flux density can be obtained.
（発明の効果）
以上説明したように本発明によるときは、降伏点８０ｋ
ｇ／ｍｍ２以上、引張強さ１００ ｋ＋ｒ／ｍｕ”以上
、磁束密度Ｂ１゜。１．７Ｔｅｓｌａ以上を有する高強
度熱延鋼板を的確に製造し得るものであるから工業的に
その効果は大きい。(Effect of the invention) As explained above, according to the present invention, the yield point is 80k.
It is possible to accurately produce high-strength hot-rolled steel sheets having a tensile strength of 100 k+r/mu" or more, a magnetic flux density of B1°.1.7 Tesla or more, and therefore has great industrial effects.
第１図はＴｉ添加鋼のＢ添加の有無および冷却速度と引
張試験値との関係を示したもので第２図はＴｉ添加鋼の
Ｂ添加の有無、Ｃ量および冷却速度と磁束密度との関係
を示したものである。
第１図
第２図
冷却遣度功ｅｃFigure 1 shows the relationship between the presence or absence of B addition in Ti-added steel, the cooling rate, and the tensile test value, and Figure 2 shows the relationship between the presence or absence of B addition, C content, cooling rate, and magnetic flux density in Ti-added steel. This shows the relationship. Figure 1 Figure 2 Cooling efficiency EC
Claims (1)
ラブを、加熱温度１２００℃以上に加熱し、熱延仕上温
度Ａｒ＿３変態点以上９５０℃以下で熱間圧延し、冷却
速度３０℃／ｓｅｃ以上７０℃／ｓｅｃ未満で冷却し、
５００℃以下で巻取ることを特徴とする高磁束密度を有
する高張力熱延鋼板の製造方法。[Claims] C: 0.05-0.15% Si: 0.50% or less Mn: 0.70-2.00% P: 0.020% or less S: 0.010% or less solAl: 0 A steel slab containing .010 to 0.10% N: 0.0050% or less Ti: 0.10 to 0.30% B: 0.0015 to 0.0050%, with the remainder consisting of Fe and unavoidable impurities, Heating to a heating temperature of 1200° C. or higher, hot rolling at a hot rolling finishing temperature Ar_3 transformation point or higher and 950° C. or lower, cooling at a cooling rate of 30° C./sec or higher and lower than 70° C./sec,
A method for producing a high-tensile hot-rolled steel sheet having a high magnetic flux density, which comprises winding at a temperature of 500°C or less.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61315806A JPS63166931A (en) | 1986-12-27 | 1986-12-27 | Manufacture of high tension hot rolled steel sheet having high magnetic flux density |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61315806A JPS63166931A (en) | 1986-12-27 | 1986-12-27 | Manufacture of high tension hot rolled steel sheet having high magnetic flux density |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS63166931A true JPS63166931A (en) | 1988-07-11 |
Family
ID=18069779
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61315806A Pending JPS63166931A (en) | 1986-12-27 | 1986-12-27 | Manufacture of high tension hot rolled steel sheet having high magnetic flux density |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63166931A (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6632295B2 (en) | 1999-09-28 | 2003-10-14 | Nkk Corporation | High tensile strength hot-rolled steel sheet and method for manufacturing the same |
| JP2010150667A (en) * | 2004-02-17 | 2010-07-08 | Nippon Steel Corp | Electromagnetic steel sheet and method for manufacturing the same |
| WO2013115205A1 (en) | 2012-01-31 | 2013-08-08 | Ｊｆｅスチール株式会社 | Hot-rolled steel for power generator rim and method for manufacturing same |
| WO2014148001A1 (en) | 2013-03-19 | 2014-09-25 | Ｊｆｅスチール株式会社 | HIGH-STRENGTH HOT ROLLED STEEL SHEET HAVING TENSILE STRENGTH OF 780 MPa OR MORE |
| KR20170072312A (en) | 2014-12-05 | 2017-06-26 | 제이에프이 스틸 가부시키가이샤 | Hot-rolled steel sheet for magnetic pole and method for manufacturing same, and rim member for hydroelectric power generation |
| KR20170072311A (en) | 2014-11-28 | 2017-06-26 | 제이에프이 스틸 가부시키가이샤 | Hot-rolled steel sheet for magnetic pole and method for manufacturing same, and rim member for hydroelectric power generation |
-
1986
- 1986-12-27 JP JP61315806A patent/JPS63166931A/en active Pending
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6632295B2 (en) | 1999-09-28 | 2003-10-14 | Nkk Corporation | High tensile strength hot-rolled steel sheet and method for manufacturing the same |
| EP1170390A4 (en) * | 1999-09-28 | 2005-02-23 | Jfe Steel Corp | Hot-rolled steel sheet having high tensile strength and method for production thereof |
| JP2010150667A (en) * | 2004-02-17 | 2010-07-08 | Nippon Steel Corp | Electromagnetic steel sheet and method for manufacturing the same |
| WO2013115205A1 (en) | 2012-01-31 | 2013-08-08 | Ｊｆｅスチール株式会社 | Hot-rolled steel for power generator rim and method for manufacturing same |
| KR20140108713A (en) | 2012-01-31 | 2014-09-12 | 제이에프이 스틸 가부시키가이샤 | Hot-rolled steel for power generator rim and method for manufacturing same |
| US10301698B2 (en) | 2012-01-31 | 2019-05-28 | Jfe Steel Corporation | Hot-rolled steel sheet for generator rim and method for manufacturing the same |
| WO2014148001A1 (en) | 2013-03-19 | 2014-09-25 | Ｊｆｅスチール株式会社 | HIGH-STRENGTH HOT ROLLED STEEL SHEET HAVING TENSILE STRENGTH OF 780 MPa OR MORE |
| EP2977481A4 (en) * | 2013-03-19 | 2016-06-22 | Jfe Steel Corp | HIGH-STRENGTH HOT ROLLED STEEL SHEET HAVING TENSILE STRENGTH OF 780 MPa OR MORE |
| KR20170069307A (en) | 2013-03-19 | 2017-06-20 | 제이에프이 스틸 가부시키가이샤 | HIGH-STRENGTH HOT ROLLED STEEL SHEET HAVING TENSILE STRENGTH OF 780 MPa OR MORE |
| US10400316B2 (en) | 2013-03-19 | 2019-09-03 | Jfe Steel Corporation | High strength hot rolled steel sheet having tensile strength of 780 MPa or more |
| KR20170072311A (en) | 2014-11-28 | 2017-06-26 | 제이에프이 스틸 가부시키가이샤 | Hot-rolled steel sheet for magnetic pole and method for manufacturing same, and rim member for hydroelectric power generation |
| KR20170072312A (en) | 2014-12-05 | 2017-06-26 | 제이에프이 스틸 가부시키가이샤 | Hot-rolled steel sheet for magnetic pole and method for manufacturing same, and rim member for hydroelectric power generation |
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