JPS62256947A - Tempered high-phosphorus-type weather-resisting steel plate excellent in weldability and toughness at low temperature - Google Patents
Tempered high-phosphorus-type weather-resisting steel plate excellent in weldability and toughness at low temperatureInfo
- Publication number
- JPS62256947A JPS62256947A JP9869786A JP9869786A JPS62256947A JP S62256947 A JPS62256947 A JP S62256947A JP 9869786 A JP9869786 A JP 9869786A JP 9869786 A JP9869786 A JP 9869786A JP S62256947 A JPS62256947 A JP S62256947A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- toughness
- weldability
- less
- tempered
- 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 52
- 239000010959 steel Substances 0.000 title claims abstract description 52
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 25
- 238000005496 tempering Methods 0.000 claims abstract description 18
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 11
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 11
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 10
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 7
- 229910052802 copper Inorganic materials 0.000 claims abstract description 6
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 6
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 6
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 6
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 5
- 229910000870 Weathering steel Inorganic materials 0.000 claims description 25
- 239000011574 phosphorus Substances 0.000 claims description 19
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 claims description 12
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 10
- 239000012535 impurity Substances 0.000 claims description 6
- 229910052742 iron Inorganic materials 0.000 claims description 5
- 238000011282 treatment Methods 0.000 abstract description 7
- 230000007797 corrosion Effects 0.000 abstract description 5
- 238000005260 corrosion Methods 0.000 abstract description 5
- 238000003466 welding Methods 0.000 abstract description 5
- 229910017813 Cu—Cr Inorganic materials 0.000 abstract description 3
- 229910052719 titanium Inorganic materials 0.000 abstract description 3
- 239000000203 mixture Substances 0.000 abstract description 2
- 239000004035 construction material Substances 0.000 abstract 2
- 230000001105 regulatory effect Effects 0.000 abstract 2
- 230000001276 controlling effect Effects 0.000 abstract 1
- 238000010791 quenching Methods 0.000 description 17
- 230000000171 quenching effect Effects 0.000 description 17
- 230000000694 effects Effects 0.000 description 14
- 239000010953 base metal Substances 0.000 description 11
- 239000000463 material Substances 0.000 description 10
- 238000005336 cracking Methods 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 5
- 230000007423 decrease Effects 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- 238000000034 method Methods 0.000 description 4
- 238000005096 rolling process Methods 0.000 description 4
- 238000005275 alloying Methods 0.000 description 3
- 150000004767 nitrides Chemical class 0.000 description 3
- 229920006395 saturated elastomer Polymers 0.000 description 3
- 230000007704 transition Effects 0.000 description 3
- 229910052684 Cerium Inorganic materials 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 229910000760 Hardened steel Inorganic materials 0.000 description 1
- 230000003679 aging effect Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000001514 detection method Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- BHEPBYXIRTUNPN-UHFFFAOYSA-N hydridophosphorus(.) (triplet) Chemical compound [PH] BHEPBYXIRTUNPN-UHFFFAOYSA-N 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 230000001939 inductive effect Effects 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000010587 phase diagram Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- -1 quenched structure Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Abstract
Description
(産業上の利用分野)
本発明は、例えば、橋梁等のような一般の大気腐食環境
において、溶接構造材料として用いるに適する溶接性及
び低温靭性に優れた鋼板で、直接焼入れ十焼もどし処理
或いはオフライン焼入れ十焼もどし処理によって製造さ
れる高燐型耐候性鋼板に関する。
(従来の技術)
従来より、か\る耐候性鋼板としては、P含有量が0.
07〜0.15%のP−Cu−Cr系鋼板が大気中での
腐食に対して優れた耐候性を有することは既によく知ら
れている。しかし、この鋼板は、上記のようにPを多量
に含有しているため、通常の焼入れ、焼戻し処理のよう
な調質熱処理を施すと、焼戻し脆化が顕著に現われ、低
温靭性が損われるという問題がある。したがって、この
種の鋼板は、熱処理を施さずに圧延ままで所定の強度を
確保する方法が採られてきた。
(発明が解決しようとする問題点)
しかし乍ら、圧延ままで鋼材の強度を高めるためには、
鋼中の合金元素量を増加させる必要があるが、合金元素
量の増加は鋼の溶接性或いは溶接継手部の低温靭性を劣
化させるため、その添加量には限度がある。したがって
、従来は、溶接性及び低温靭性を考慮して高燐型耐候性
鋼板は引張強さ50キロ級までのものに制限されて製造
されてきた。
一方、この種の耐候性鋼板に要求される引張強さは、最
近では、60キロにまで及んでおり、溶接性及び低温靭
性に優れた高燐型60キロ級耐候性鋼板に対する需要家
の要求は強いものがある。
本発明は、か\る要請に応えるべくなされたものであっ
て、上記高燐型耐候性鋼板の焼戻し脆化の問題を高価な
合金元素の添加によらず、微量のBの活用と焼入組織の
コントロールによって解決し、従来は行われていなかっ
た焼入、焼戻し処理を施して製造できる溶接性及び低温
靭性に優れた調質50キロ級及び60キロ級高燐型耐候
性鋼板を提供することを目的とするものである。
(問題点を解決するための手段)
前述の如く、従来の高燐型耐候性鋼に焼入、焼戻し処理
を施すと圧延まま材に比べて脆化するが、この脆化はい
わゆる焼戻し脆性によるものである。
焼戻し脆化の原因の1つとしては、Ac工点点以下温度
に加熱時にPなどの不純物元素が旧γ粒界に偏析し、粒
界を脆くして粒界破壊を誘発するためであると云われて
いる。
そこで、本発明者らは、Bのγ粒界への偏析に着目し、
高燐型耐候性鋼にBを添加したものと添加しないものに
ついて通常の焼入、焼戻し処理を実施し、低温靭性を調
査した。なお、該謂は0.07%C−0,08%P−0
.3%Cu−0.4%Crを基本成分とし、これにBの
添加量を変えたものについて、焼入(930℃)、焼も
どしく640℃)を施した。
その結果、第1図に示すように、Bを添加したものは、
Bを添加しないものに比べて破面遷移温度(vTrs)
が最大40℃低温側に移行しており、優れた低温靭性を
示すことが明らかとなった。
この理由については、900℃以上の温度に加熱時にB
がPよりも先にγ粒界に偏析し、粒界エネルギーを低下
させ、Pのγ粒界への偏析が抑制されるため、粒界が脆
くならないことによるものと考えられる。
一方、本発明者らの研究によれば、B含有高燐型耐候性
鋼を焼入、焼戻し処理した材料の低温靭性は、焼入組織
とよく対応していることが明らかとなった。すなわち、
第2図に示すように、焼入まま材の組織中のマルテンサ
イト+ベーナイト量が90%以上の場合、焼戻し後の鋼
板の遷移温度(vTrs)は−60℃以下であり、良好
な低温靭性を有している。
この原因については、十分に解明されるまでには至って
いないが、以下■、■のように考えられる。
■ 第3図に示すFe−P状態図から明らかなように、
加熱温度930℃の場合、P含有:to。
10%の鋼の組織は図中ので示すようにγ+αからなる
2相である。この場合、α中のpa度はγ中のものに比
べ著しく高くなる。
■ P濃度の高いαの靭性はP濃度の低い他の組織のも
のに比べて低いことが予想され、これが破壊の起点とな
り、その量が10%を超えて存在すると急激に低温靭性
が低下する。
このように、焼戻し脆化を起こし易い高燐型耐候性鋼の
鋼中に適量のBを添加し、更に焼入組織をコントロール
することによって、遷移温度(vTrs)が60℃以下
の如く良好な低温靭性を有し、また溶接性も優れたする
調質高燐型耐候性鋼板が得られることを知見し、この知
見に基づいて更に実験研究を重ね、ここに本発明をなし
たものである。
すなわち、本発明に係る溶接性及び低温靭性に優れた調
質高燐型耐候性鋼板は、C:0.02〜0.10%、S
L:0.75%以下、Mn:0.5〜1.5%、P:0
.04〜0.15%、 Cu:Q、15〜0.6%、C
r:0.1〜1.0%及びB:0.0OO3〜0.00
20%を含有し、更に必要に応じて、Ce:0.OOl
〜0.L%及びCa:0.004%以下のうちの1種
又は2種と、及びl又は、Ti:0.002〜0.05
%、Zr:0.OO2〜0.05%、Ni:0.05〜
1.0%、Mo:0.05〜0.5%、V:0.01〜
0.15%及びNb:0.01〜0.15%のうちの1
種又は2種以上を含有し。
かつ、炭素当量Ceq (=C+1/24Si+1/6
Mn+1/40Ni+115Cr+1/4Mo+1/1
4V)(%)が0.40%以下で、残部が鉄及び不可避
的不純物よりなる焼入れ、焼戻し鋼であって、焼入組織
においてマルテンサイト+ベーナイト量が90%以上の
ものを焼戻してなることを特徴とするものである。
以下に本発明を実施例に基づいて詳細に説明する。
まず、本発明に係る高燐型耐候性鋼板の成分限定理由に
ついて説明する。
Cは、溶接性及び低温靭性の双方の面からできるだけ少
ないことが望ましく1本発明の目的を達成するためには
、その上限を0.10%とする必要がある。しかし、C
含有量が0.02%未満の場合には、母材強度を確保で
きないので、その下限を0.02%とする。
Siは、溶鋼の脱酸及び鋼板の強度向上に有効な元素で
あるが、0.75%を超えて添加してもその効果は少な
く、却って溶接性や低温靭性を劣化させるので、その上
限を0.75%とする。
Mnは、その含有量が0.5%よりも少ないときは、高
燐型耐候性鋼板の?8接時の耐高温割れ性の改善及び母
材強度の確保が望めず、また、1.5%を超えて添加し
てもその効果は飽和傾向にあり、逆に溶接継手部の靭性
が劣化するので、その範囲を0.5〜1.5%とする。
Pは、耐候性の向上の観点から好ましい元素であり、こ
の含有量を少なくすると大気中における耐候性が低下す
るので、少なくとも0.04%は必要である。しかし、
0.15%を超えて添加しても耐候性向上効果は飽和し
、却って溶接性及び低温靭性の劣化が著しくなる。した
がって、その範囲を0.04〜0.15%とする。
Cuは、Pと共に耐候性の向上に有効な元素であり、最
少限0.15%は必要である。しかし、0.60%を超
えて添加してもその効果は期待できず、却って時効性及
び熱間圧延時の表面ひび割れ等が生じるので、その範囲
を0.15〜0.60%とする。
Crは、その含有量の増加と共に耐候性を向上させるが
、0.1%未満では耐候性の効果は小さく、一方、1.
0%を超えて添加すると溶接性が著しく劣化するので好
ましくない、したがって、その範囲を0.1〜1.0%
とする。
Bは、前述したように、高燐型耐候性鋼板の焼入、焼も
どし処理材の低温靭性を著しく改善するのに有効であり
、最少限0.0003%は必要である。しかし、0.0
020%を超えて添加すると、B化合物が増加し、溶接
継平部靭性のみならず、母材靭性をも著しく劣化させる
ので、その上限を0.0020%とする。
炭素当量Ceq(=C+1/24Si+1/6Mn+1
/40Ni+115Cr+1/4Mo+1/14V)(
%)を0.40%以下としたのは、Ceqの低減が高燐
型耐候性鋼板の溶接性及び溶接継手部の靭性向上に極め
て有効であり、Ceqが0.40%を超えると、これら
の特性が著しく劣化し、本発明の目的が達成できなくな
るためである。
また、焼入れ組織においてマルテンサイト+ベーナイト
量を90%以上(フェライト量10%以下)に規制した
のは、前述のように、マルテンサイト+ベーナイト量が
90%未満の場合には良好な低温靭性が得られなくなる
からである。このような組織は、加熱温度を例えば95
0℃以上に高めて焼入れする方法、或いは圧延後950
℃程度の温度から直接焼入れする方法等によって得るこ
とができる。また、焼戻しは上記焼入鋼をA C1点以
下の温度で行うのが好ましい。
なお、本発明に係る溶接性及び低温靭性に優れた調質高
燐型耐候性鋼板には、上記の必須元素に加えて、必要に
応じて更に、Ca及びCeよりなる群から選ばれる少な
くとも1種の元素を含有させることができる。これらの
元素は、酸硫化物形成元素であるので、これらを添加す
ることにより、介在物の性質及び形状を改善し、溶接部
の高温割れ感受性、母材のZ方向特性、及び母材とHA
Z(熱影響部)の靭性を一層向上させることができる。
Caは、例えば、Ca−3i、Ca(CN)、、CaC
。
等のような合金化合物の形態で溶鋼中に0.5〜20k
g/溶鋼トン程度投入することにより1通常。
得られる鋼中にCaが0.004%以下の含有量にて残
留する。上記のように、介在物の性質及び形状を制御す
るためには、上記量を超えて多量に添加する必要がない
ので、Caの添加量の上限は0゜004%とする。
Ceは、その添加量が0.001%未満のときは、上記
のような介在物制御効果が乏しく、他方。
0.1%を超えて多量に添加すると、m塊の底部にCe
S等の大型介在物が集積し、鋼板の超音波探傷欠陥の原
因となるので、添加量はO0O○1〜0.1%の範囲と
する。
更に、本発明鋼は、必要に応じ、上記の任意添加元素と
は別に、又は任意添加元素と共に、Tj。
Zr、 Ni、 Mo、 V及びNbよりなる群から選
ばれる少なくとも1種の元素をHAZ靭性を損なわない
程度に含有させることができる。
T1及びZrは、共に窒化物を形成して、大入熱溶接時
のHAZ靭性向上に有効な元素である。かかる効果を有
効に発現させるためには、それぞれ少なくとも0.00
2%を添加することが必要であるが、他方、それぞれ0
.05%を超えて過多に添加すると、Ti又はZrの非
金属介在物の増加と共に大きい窒化物が析出し、HAZ
靭性が劣化するばかりでなく、母材靭性も低下する6し
たがって、本発明においては、Ti又はZrの添加量は
、それぞれ0.002〜0.05%の範囲とする。
Niは、耐候性、母材強度、母材切欠靭性及びHA Z
靭性向上に効果を有するので、これらの要求に応じて広
範囲にその添加量を変化させて含有させることができる
。上記効果を有効に得るためには、少なくとも0.05
%以上を添加する必要があるが、余りに多量に添加して
もその効果が飽和し、また、経済性の点からも好ましく
ないので、添加量の上限を1.0%とする。
Moは、少量の添加にて母材強度を著しく向上させるの
で、厚物の強度確保に有効な元素である。
この効果を有効に得るためには、少なくとも0゜05%
以上を添加する必要があるが、余りに多量に添加すると
、HAZ靭性が劣化するので、添加量の上限は0.5%
とする。
■及びNbは、共に窒化物を形成して、溶接部の軟化防
止、母材強度の向上、更には低Ceq化による耐溶接割
れ性の向上を図ることができる。かかる効果を有効に発
現させるためには、それぞれ少なくとも0.01%を添
加することが必要である。しかし、それぞれ0.15%
を超えて過多に添加しても、母材強度の向上効果が顕著
には増大せず、却って溶接性の劣化やHAZ靭性の低下
を招く。したがって1本発明においては、Nb及びVは
それぞれ0.01%〜0.15%の範囲で添加する。
以上の条件を満たす本発明鋼板は、溶接性及び低温靭性
に優れた調質高燐型耐候性鋼板であって。
通常の製鋼、分塊圧延、焼入れ一焼戻し処理或いは圧延
後直接焼入れ一焼戻し処理によって製造することができ
、引張強さ50〜60 kgf / mm”級の強度を
付与することができる。
(実施例)
次に本発明の一実施例を示すが、本発明はこれらの実施
例によって何ら制限されるものでないことは云うまでも
ない。
去】u」1
第1表に本発明鋼Nα1〜8、従来fllNα9及び比
較鋼Na1o〜12の化学成分、焼入組織、母材特性及
び溶接性を示す、名調は、圧延後直接焼入れ(焼入温度
950”C)或いはオフライン焼入れ(焼入温度930
℃、950’C)を行った後、640℃で焼戻し処理を
施したものである。
なお、溶接性は、JIS規格に制定されている斜めY型
拘束突合せ溶接割れ試験(低温割れ試験)によって評価
した。
同表に示す試験結果によれば、本発明鋼の母材の一40
℃における吸収エネルギー(vE−4゜)は12kgf
−m以上であり、従来鋼Nα9及び比較鋼勲10.11
の値に比べて格段に優れていることが明らかである。
また、従来鋼の低温割れ防止余熱温度が100℃である
のに対して、本発明鋼はいずれも50℃以下であって、
優れた耐低温割れ感受性を有していることが明白である
。
強度レベルについては、本発明鋼は、圧延後直接焼入れ
十焼戻し処理、或いは焼入温度950℃のオフライン焼
入れ十焼戻し処理によって50kgf/mm”級及び6
0kgf/mm”級の引張強さが得られている。(Industrial Application Field) The present invention is a steel plate with excellent weldability and low-temperature toughness that is suitable for use as a welding structural material in general atmospheric corrosive environments such as bridges, etc. The present invention relates to a high phosphorus type weathering steel sheet manufactured by off-line quenching and tempering treatment. (Prior Art) Conventionally, weathering steel sheets have a P content of 0.
It is already well known that P-Cu-Cr steel sheets containing 0.07 to 0.15% have excellent weather resistance against corrosion in the atmosphere. However, since this steel sheet contains a large amount of P as mentioned above, when subjected to tempering heat treatment such as normal quenching and tempering, tempering embrittlement appears markedly and low-temperature toughness is impaired. There's a problem. Therefore, a method has been adopted for this type of steel plate to ensure a predetermined strength as rolled without heat treatment. (Problem to be solved by the invention) However, in order to increase the strength of steel as rolled,
It is necessary to increase the amount of alloying elements in the steel, but since increasing the amount of alloying elements deteriorates the weldability of the steel or the low-temperature toughness of the welded joint, there is a limit to the amount that can be added. Therefore, in consideration of weldability and low-temperature toughness, high-phosphorus weathering steel sheets have conventionally been produced with a tensile strength of up to 50 kg. On the other hand, the tensile strength required for this type of weathering steel sheet has recently reached 60 kg, and customers are demanding high phosphorus type 60 kg weathering steel sheet with excellent weldability and low-temperature toughness. There is something strong about it. The present invention has been made in response to such demands, and solves the problem of temper embrittlement of high phosphorus weathering steel sheets by utilizing a trace amount of B and quenching without adding expensive alloying elements. To provide tempered 50 kg class and 60 kg class high phosphorous type weathering steel sheets with excellent weldability and low-temperature toughness that can be solved by microstructural control and can be manufactured by performing quenching and tempering treatments that have not been performed in the past. The purpose is to (Means for solving the problem) As mentioned above, when conventional high-phosphorus weathering steel is quenched and tempered, it becomes brittle compared to as-rolled material, but this embrittlement is due to so-called tempering embrittlement. It is something. One of the causes of temper embrittlement is said to be that impurity elements such as P segregate at prior γ grain boundaries when heated to a temperature below the AC working point, making the grain boundaries brittle and inducing intergranular fracture. It is being said. Therefore, the present inventors focused on the segregation of B to the γ grain boundaries,
Conventional quenching and tempering treatments were performed on high-phosphorus weathering steel with and without B added, and the low-temperature toughness was investigated. In addition, the so-called 0.07%C-0.08%P-0
.. Hardening (930°C) and tempering (640°C) were performed using 3% Cu-0.4% Cr as the basic component and varying the amount of B added thereto. As a result, as shown in Figure 1, the B-added product was
Fracture surface transition temperature (vTrs) compared to that without B addition
It has become clear that the temperature has shifted to the lower temperature side of 40° C., indicating excellent low-temperature toughness. The reason for this is that when heated to a temperature of 900℃ or higher, B
This is thought to be due to the fact that P segregates at the γ grain boundaries before P, lowering the grain boundary energy, and suppressing the segregation of P at the γ grain boundaries, so that the grain boundaries do not become brittle. On the other hand, the research conducted by the present inventors has revealed that the low-temperature toughness of a material obtained by quenching and tempering B-containing high-phosphorus weathering steel corresponds well to the quenched structure. That is,
As shown in Figure 2, when the amount of martensite + bainite in the structure of the as-quenched material is 90% or more, the transition temperature (vTrs) of the steel plate after tempering is -60°C or less, and it has good low-temperature toughness. have. The causes of this have not yet been fully elucidated, but are thought to be as follows. ■ As is clear from the Fe-P phase diagram shown in Figure 3,
When the heating temperature is 930°C, P content: to. The structure of 10% steel is a two-phase structure consisting of γ+α, as shown in the figure. In this case, the degree of pa in α is significantly higher than that in γ. ■ The toughness of α, which has a high P concentration, is expected to be lower than that of other structures with a low P concentration, and this becomes the starting point for fracture, and if the amount exceeds 10%, the low temperature toughness decreases rapidly. . In this way, by adding an appropriate amount of B to high-phosphorous weathering steel that is prone to temper embrittlement and further controlling the quenched structure, it is possible to achieve a good transition temperature (vTrs) of 60°C or less. It was discovered that a tempered high phosphorus type weathering steel sheet having low temperature toughness and excellent weldability can be obtained, and based on this knowledge, further experimental research was carried out, and the present invention was hereby made. . That is, the tempered high phosphorus type weathering steel sheet having excellent weldability and low-temperature toughness according to the present invention has C: 0.02 to 0.10%, S
L: 0.75% or less, Mn: 0.5-1.5%, P: 0
.. 04-0.15%, Cu:Q, 15-0.6%, C
r: 0.1-1.0% and B: 0.0OO3-0.00
20%, and further contains Ce:0. OOl
~0. One or two of L% and Ca: 0.004% or less, and L or Ti: 0.002 to 0.05
%, Zr: 0. OO2~0.05%, Ni:0.05~
1.0%, Mo: 0.05-0.5%, V: 0.01-
0.15% and Nb: 1 of 0.01-0.15%
Contains one species or two or more species. And carbon equivalent Ceq (=C+1/24Si+1/6
Mn+1/40Ni+115Cr+1/4Mo+1/1
4V) Hardened and tempered steel with (%) of 0.40% or less, the balance being iron and unavoidable impurities, and made by tempering a steel in which the amount of martensite + bainite in the quenched structure is 90% or more. It is characterized by: The present invention will be explained in detail below based on examples. First, the reason for limiting the components of the high phosphorus weathering steel sheet according to the present invention will be explained. It is desirable that C be as small as possible from the standpoint of both weldability and low-temperature toughness.In order to achieve the object of the present invention, the upper limit should be 0.10%. However, C
If the content is less than 0.02%, the strength of the base material cannot be ensured, so the lower limit is set to 0.02%. Si is an effective element for deoxidizing molten steel and improving the strength of steel sheets, but adding more than 0.75% will have little effect and will actually deteriorate weldability and low-temperature toughness, so the upper limit should not be set. It shall be 0.75%. When the content of Mn is less than 0.5%, what is the content of Mn in high phosphorus weathering steel sheet? It is not possible to improve the hot cracking resistance during 8 welding and ensure the strength of the base metal, and even if it is added in excess of 1.5%, the effect tends to be saturated, and on the contrary, the toughness of the welded joint deteriorates. Therefore, the range is set to 0.5 to 1.5%. P is a preferable element from the viewpoint of improving weather resistance, and if its content is reduced, weather resistance in the atmosphere will decrease, so at least 0.04% is required. but,
Even if it is added in an amount exceeding 0.15%, the effect of improving weather resistance is saturated, and on the contrary, the deterioration of weldability and low-temperature toughness becomes significant. Therefore, the range is set to 0.04 to 0.15%. Cu, together with P, is an element effective in improving weather resistance, and a minimum content of 0.15% is required. However, even if it is added in an amount exceeding 0.60%, no effect can be expected, and on the contrary, aging properties and surface cracks during hot rolling will occur, so the range is set to 0.15 to 0.60%. Cr improves weather resistance as its content increases, but if it is less than 0.1%, the effect on weather resistance is small;
Adding more than 0% is not preferable as it will significantly deteriorate weldability. Therefore, the range should be reduced to 0.1 to 1.0%.
shall be. As mentioned above, B is effective in significantly improving the low-temperature toughness of quenched and tempered high-phosphorus weathering steel sheets, and a minimum amount of 0.0003% is required. However, 0.0
If added in excess of 0.020%, the B compound will increase and will significantly deteriorate not only the toughness of the weld joint but also the toughness of the base metal, so the upper limit is set at 0.0020%. Carbon equivalent Ceq (=C+1/24Si+1/6Mn+1
/40Ni+115Cr+1/4Mo+1/14V)(
%) is set to 0.40% or less because reducing Ceq is extremely effective in improving the weldability of high-phosphorus weathering steel sheets and the toughness of welded joints, and when Ceq exceeds 0.40%, these This is because the characteristics of the material deteriorate significantly, making it impossible to achieve the object of the present invention. In addition, the reason why the amount of martensite + bainite is restricted to 90% or more (the amount of ferrite is 10% or less) in the quenched structure is because, as mentioned above, when the amount of martensite + bainite is less than 90%, good low-temperature toughness is achieved. This is because you will not be able to obtain it. Such a structure is heated at a heating temperature of, for example, 95
A method of quenching at a temperature of 0℃ or higher, or a method of quenching at 950℃ after rolling.
It can be obtained by a method such as direct quenching at a temperature of about ℃. Further, it is preferable that the above-mentioned hardened steel be tempered at a temperature below the AC1 point. In addition to the above-mentioned essential elements, the tempered high-phosphorus weathering steel sheet having excellent weldability and low-temperature toughness according to the present invention further contains at least one element selected from the group consisting of Ca and Ce, if necessary. Seed elements can be contained. These elements are oxysulfide-forming elements, so their addition improves the properties and shape of inclusions, improves the hot cracking susceptibility of the weld, the Z-direction properties of the base metal, and the relationship between the base metal and HA.
The toughness of Z (heat affected zone) can be further improved. Ca is, for example, Ca-3i, Ca(CN), CaC
. 0.5-20k in molten steel in the form of alloy compounds such as
1 usually by adding about g/ton of molten steel. Ca remains in the resulting steel at a content of 0.004% or less. As mentioned above, in order to control the properties and shapes of inclusions, it is not necessary to add more than the above amount, so the upper limit of the amount of Ca added is 0°004%. On the other hand, when the amount of Ce added is less than 0.001%, the effect of controlling inclusions as described above is poor. If added in a large amount exceeding 0.1%, Ce will be added to the bottom of the m block.
Since large inclusions such as S accumulate and cause ultrasonic flaw detection defects in steel plates, the amount added is in the range of 00O1 to 0.1%. Furthermore, the steel of the present invention may contain Tj, in addition to or together with the above-mentioned optionally added elements, if necessary. At least one element selected from the group consisting of Zr, Ni, Mo, V, and Nb can be contained to an extent that does not impair HAZ toughness. Both T1 and Zr form nitrides and are effective elements for improving HAZ toughness during high heat input welding. In order to effectively express such effects, each of at least 0.00
It is necessary to add 2%, but on the other hand, each 0
.. If added in excess of 0.5%, large nitrides will precipitate as well as non-metallic inclusions of Ti or Zr, resulting in HAZ
Not only the toughness deteriorates, but also the toughness of the base material decreases.6 Therefore, in the present invention, the amount of Ti or Zr added is in the range of 0.002 to 0.05%, respectively. Ni improves weather resistance, base metal strength, base metal notch toughness, and HAZ
Since it is effective in improving toughness, it can be added in a wide range of amounts depending on these requirements. In order to effectively obtain the above effect, at least 0.05
% or more, but if too much is added, the effect will be saturated and it is also unfavorable from an economic point of view, so the upper limit of the amount added is set at 1.0%. Mo significantly improves the strength of the base material when added in a small amount, so it is an effective element for ensuring the strength of thick products. In order to effectively obtain this effect, at least 0.05%
It is necessary to add the above, but if too large a amount is added, the HAZ toughness will deteriorate, so the upper limit of the amount added is 0.5%.
shall be. (2) and Nb together form nitrides, which can prevent softening of the weld zone, improve base metal strength, and further improve weld cracking resistance by lowering Ceq. In order to effectively exhibit such effects, it is necessary to add at least 0.01% of each. However, each 0.15%
Even if it is added in excess of more than 100%, the effect of improving base metal strength will not increase significantly, but will instead cause deterioration of weldability and decrease in HAZ toughness. Therefore, in the present invention, Nb and V are each added in a range of 0.01% to 0.15%. The steel sheet of the present invention that satisfies the above conditions is a tempered high-phosphorous weathering steel sheet that has excellent weldability and low-temperature toughness. It can be manufactured by ordinary steel manufacturing, blooming rolling, quenching and tempering treatment, or directly quenching and tempering treatment after rolling, and can be given a tensile strength of 50 to 60 kgf/mm'' class. (Example) ) Next, one example of the present invention will be shown, but it goes without saying that the present invention is not limited in any way by these examples. The chemical composition, quenched structure, base material properties, and weldability of conventional fllNα9 and comparative steels Na1o to 12 are shown by direct quenching after rolling (quenching temperature 950"C) or off-line quenching (quenching temperature 930"C).
950'C) and then tempered at 640°C. The weldability was evaluated by a diagonal Y-type restrained butt weld cracking test (low-temperature cracking test) established in JIS standards. According to the test results shown in the same table, the base material of the steel of the present invention was 40%
Absorbed energy (vE-4°) at °C is 12 kgf
−m or more, conventional steel Nα9 and comparative steel Nα10.11
It is clear that the value is much better than that of . In addition, while the preheat temperature for preventing cold cracking of conventional steel is 100°C, the steel of the present invention has a preheat temperature of 50°C or less,
It is clear that it has excellent cold cracking resistance and susceptibility. Regarding the strength level, the steel of the present invention has a strength level of 50 kgf/mm" class and 6.
A tensile strength of 0 kgf/mm'' class was obtained.
次に、第1表に示した鋼板について、入熱量45KJ/
cmサブマージアーク溶接継手ボンド部の一20℃にお
ける吸収エネルギー(vE−2a)及び発露型腐食試験
による腐食度を第2表に示す。
同表より、サブマージアーク溶接継手ボンド部の衝撃特
性については、従来鋼及び比較鋼に比べて本発明鋼が格
段に優れた衝撃特性を有していることが明らかである。
一方、比較gllNα10は1本発明鋼に比べて焼入組
織のマルテンサイト+ベーナイト量が80%と少ないの
で、溶接性及び耐候性は本発明鋼とはゾ同等であっても
、母材靭性及び継手ボンド部の衝撃特性が著しく劣って
いる。
更に、発露型腐食試験機を用いて、海洋工業地帯を想定
した条件下で行った試験期間6週間の促進試験結果によ
れば、本発明鋼が従来鋼Nα9に比べて同等以上の耐候
性を有し、しかも、本発明鋼は、比較鋼(JIS 5
MA30)に比べて、1.5倍の優れた耐候性を有して
いることが明らかである。
第 2 表
(発明の効果)
以上詳述したように、本発明によれば、P−Cu−Cr
系の高燐型耐候性鋼板において、特に低C化と共に低C
eq化し、かつ、微量のBの添加活用と焼入組織のコン
トロールにより、溶接性及び低温靭性が著しく改善され
た調質50〜60kgf/m2級鋼板を得ることができ
る。特に、かNる耐候性鋼板は、耐候性、高強度、溶接
性及び低温靭性が要求される橋梁、建築物、鉄塔等々の
構造物への使用に好適である。Next, regarding the steel plate shown in Table 1, the heat input is 45KJ/
Table 2 shows the absorbed energy (vE-2a) of the bond part of the cm submerged arc welded joint at 120°C and the degree of corrosion determined by the dew corrosion test. From the same table, it is clear that the steel of the present invention has much better impact properties than the conventional steel and comparative steel with respect to the impact properties of the bonded portion of submerged arc welded joints. On the other hand, comparative gllNα10 has a lower amount of martensite + bainite in the quenched structure than the inventive steel, at 80%, so even though the weldability and weather resistance are comparable to the inventive steel, the base metal toughness and The impact properties of the joint bond area are extremely poor. Furthermore, according to the results of an accelerated test conducted over a 6-week period using a dew-type corrosion tester under conditions simulating a marine industrial zone, the steel of the present invention has weather resistance equal to or higher than that of the conventional steel Nα9. Moreover, the steel of the present invention has a comparative steel (JIS 5
It is clear that it has 1.5 times better weather resistance than MA30). Table 2 (Effects of the Invention) As detailed above, according to the present invention, P-Cu-Cr
In high phosphorus type weathering steel sheets, especially low C and low C
By adding a small amount of B and controlling the quenched structure, it is possible to obtain a heat-treated 50-60 kgf/m2 grade steel plate with significantly improved weldability and low-temperature toughness. In particular, the weathering steel plate is suitable for use in structures such as bridges, buildings, and steel towers that require weather resistance, high strength, weldability, and low-temperature toughness.
第1図は0.07%C−0,08%P−0.30%Cu
−0.4%Cr系鋼にBを添加したものと添加しないも
のについて通常の焼入れ、焼戻し処理を実施し、母材衝
撃特性値(vTrs)に及ぼすB含有量の影響を示した
図、
第2図は、第1図に示した0、0010%B含有鋼につ
いて焼入温度を変化させて得られた焼入組織のマルテン
サイト+ベーナイト量と母材衝撃特性値(vTrs)の
関係を示した図、第3図はFe−P状j原図である。
特許出願人 株式会社神戸製鋼所
代理人弁理士 中 村 尚
第1図
B合哨量 (PPm)
第2図Figure 1 shows 0.07%C-0.08%P-0.30%Cu
A diagram showing the effect of B content on the base metal impact properties (vTrs) when normal quenching and tempering treatments were carried out on -0.4% Cr steel with and without B added. Figure 2 shows the relationship between the amount of martensite + bainite in the quenched structure and the base metal impact characteristic value (vTrs) obtained by varying the quenching temperature for the 0,0010% B-containing steel shown in Figure 1. The above figure and FIG. 3 are the original drawings of the Fe-P shape. Patent applicant Takashi Nakamura, Patent attorney representing Kobe Steel, Ltd. Figure 1 B Combined amount (PPm) Figure 2
Claims (4)
0%、Si:0.75%以下、Mn:0.5〜1.5%
、P:0.04〜0.15%、Cu:0.15〜0.6
0%、Cr:0.1〜1.0%及びB:0.0003〜
0.0020%を含有し、かつ、炭素当量Ceq(=C
+1/24Si+1/6Mn+1/40Ni+1/5C
r+1/4Mo+1/14V)(%)が0.40%以下
で、残部が鉄及び不可避的不純物よりなる焼入れ、焼戻
し鋼であって、焼入組織においてマルテンサイト+ベー
ナイト量が90%以上であるものを焼戻してなることを
特徴とする溶接性及び低温靭性に優れた調質高燐型耐候
性鋼板。(1) In weight% (the same applies hereinafter), C: 0.02 to 0.1
0%, Si: 0.75% or less, Mn: 0.5-1.5%
, P: 0.04-0.15%, Cu: 0.15-0.6
0%, Cr: 0.1-1.0% and B: 0.0003-
0.0020%, and carbon equivalent Ceq (=C
+1/24Si+1/6Mn+1/40Ni+1/5C
Hardened and tempered steel in which r+1/4Mo+1/14V) (%) is 0.40% or less, the balance being iron and unavoidable impurities, and the amount of martensite + bainite in the quenched structure is 90% or more. A heat-treated high phosphorus weathering steel sheet with excellent weldability and low-temperature toughness, characterized by being tempered.
下、Mn:0.5〜1.5%、P:0.04〜0.15
%、Cu:0.15〜0.60%、Cr:0.1〜1.
0%及びB:0.0003〜0.0020%を含有し、
更にCe:0.001〜0.1%及びCa:0.004
%以下のうちの1種又は2種を含有し、かつ、炭素当量
Ceq(=C+1/24Si+1/6Mn+1/40N
i+1/5Cr+1/4Mo+1/14V)(%)が0
.40%以下で、残部が鉄及び不可避的不純物よりなる
焼入れ、焼戻し鋼であって、焼入組織においてマルテン
サイト+ベーナイト量が90%以上であるものを焼戻し
てなることを特徴とする溶接性及び低温靭性に優れた調
質高燐型耐候性鋼板。(2) C: 0.02-0.10%, Si: 0.75% or less, Mn: 0.5-1.5%, P: 0.04-0.15
%, Cu: 0.15-0.60%, Cr: 0.1-1.
0% and B: 0.0003 to 0.0020%,
Furthermore, Ce: 0.001 to 0.1% and Ca: 0.004
% or less, and carbon equivalent Ceq (=C + 1/24Si + 1/6Mn + 1/40N
i+1/5Cr+1/4Mo+1/14V) (%) is 0
.. 40% or less, the balance being iron and unavoidable impurities, the weldability and tempering steel is made by tempering a steel whose quenched structure has a martensite + bainite content of 90% or more. Tempered high phosphorus weathering steel plate with excellent low temperature toughness.
下、Mn:0.5〜1.5%、P:0.04〜0.15
%、Cu:0.15〜0.60%、Cr:0.1〜1.
0%及びB:0.0003〜0.0020%を含有し、
更にTi:0.002〜0.05%、Zr:0.002
〜0.05%、Ni:0.05〜1.0%、Mo:0.
05〜0.50%、V:0.01〜0.15%及びNb
:0.01〜0.15%のうちの1種又は2種以上を含
有し、かつ、炭素当量Ceq(=C+1/24Si+1
/6Mn+1/40Ni+1/5Cr+1/4Mo+1
/14V)(%)が0.40%以下で、残部が鉄及び不
可避的不純物からなる焼入れ、焼戻し鋼であって、焼入
組織においてマルテンサイト+ベーナイト量が90%以
上のものを焼戻してなることを特徴とする溶接性及び低
温靭性に優れた調質高燐型耐候性鋼板。(3) C: 0.02-0.10%, Si: 0.75% or less, Mn: 0.5-1.5%, P: 0.04-0.15
%, Cu: 0.15-0.60%, Cr: 0.1-1.
0% and B: 0.0003 to 0.0020%,
Furthermore, Ti: 0.002 to 0.05%, Zr: 0.002
~0.05%, Ni: 0.05~1.0%, Mo: 0.
05-0.50%, V: 0.01-0.15% and Nb
: Contains one or more of 0.01 to 0.15%, and carbon equivalent Ceq (=C+1/24Si+1
/6Mn+1/40Ni+1/5Cr+1/4Mo+1
/14V) (%) is 0.40% or less, the balance is iron and unavoidable impurities, and the tempered steel has a martensite + bainite content of 90% or more in the quenched structure. A tempered high phosphorus type weathering steel sheet with excellent weldability and low temperature toughness.
下、Mn:0.5〜1.5%、P:0.04〜0.15
%、Cu:0.15〜0.60%、Cr:0.1〜1.
0%及びB:0.0003〜0.0020%を含有し、
更にCe:0.001〜0.1%及びCa:0.004
%以下のうちの1種又は2種と、Ti:0.002〜0
.05%、Zr:0.002〜0.05%、Ni:0.
05〜1.0%、Mo:0.05〜0.50%、V:0
.01〜0.15%及びNb:0.01〜0.15%の
うちの1種又は2種以上を含有し、かつ、炭素当量Ce
q(=C+1/24Si+1/6Mn+1/40Ni+
1/5Cr+1/4Mo+1/14V)(%)が0.4
0%以下で、残部が鉄及び不可避的不純物よりなる焼入
れ、焼戻し鋼であって、焼入組織においてマルテンサイ
ト+ベーナイト量が90%以上であるものを焼戻してな
ることを特徴とする溶接性及び低温靭性に優れた調質高
燐型耐候性鋼板。(4) C: 0.02-0.10%, Si: 0.75% or less, Mn: 0.5-1.5%, P: 0.04-0.15
%, Cu: 0.15-0.60%, Cr: 0.1-1.
0% and B: 0.0003 to 0.0020%,
Furthermore, Ce: 0.001 to 0.1% and Ca: 0.004
% or less and Ti: 0.002 to 0
.. 05%, Zr: 0.002-0.05%, Ni: 0.05%, Zr: 0.002-0.05%, Ni: 0.
05-1.0%, Mo: 0.05-0.50%, V: 0
.. 01 to 0.15% and Nb: 0.01 to 0.15%, and carbon equivalent Ce
q(=C+1/24Si+1/6Mn+1/40Ni+
1/5Cr+1/4Mo+1/14V) (%) is 0.4
0% or less, the balance being iron and unavoidable impurities, the hardened and tempered steel is made by tempering a steel whose quenched structure has a martensite + bainite content of 90% or more. Tempered high phosphorus weathering steel plate with excellent low temperature toughness.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP9869786A JPS62256947A (en) | 1986-04-28 | 1986-04-28 | Tempered high-phosphorus-type weather-resisting steel plate excellent in weldability and toughness at low temperature |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP9869786A JPS62256947A (en) | 1986-04-28 | 1986-04-28 | Tempered high-phosphorus-type weather-resisting steel plate excellent in weldability and toughness at low temperature |
Publications (1)
Publication Number | Publication Date |
---|---|
JPS62256947A true JPS62256947A (en) | 1987-11-09 |
Family
ID=14226698
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP9869786A Pending JPS62256947A (en) | 1986-04-28 | 1986-04-28 | Tempered high-phosphorus-type weather-resisting steel plate excellent in weldability and toughness at low temperature |
Country Status (1)
Country | Link |
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JP (1) | JPS62256947A (en) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2000061829A1 (en) * | 1999-04-08 | 2000-10-19 | Kawasaki Steel Corporation | Atmospheric corrosion resistant steel product |
US6699338B2 (en) | 1999-04-08 | 2004-03-02 | Jfe Steel Corporation | Method of manufacturing corrosion resistant steel materials |
CN100404700C (en) * | 2005-08-30 | 2008-07-23 | Bpw(梅州)车轴有限公司 | Heat treatment process for raising comprehensive performace of low alloy structure steel |
-
1986
- 1986-04-28 JP JP9869786A patent/JPS62256947A/en active Pending
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2000061829A1 (en) * | 1999-04-08 | 2000-10-19 | Kawasaki Steel Corporation | Atmospheric corrosion resistant steel product |
AU768461B2 (en) * | 1999-04-08 | 2003-12-11 | Jfe Steel Corporation | Corrosion resistant steel materials |
US6699338B2 (en) | 1999-04-08 | 2004-03-02 | Jfe Steel Corporation | Method of manufacturing corrosion resistant steel materials |
CN100404700C (en) * | 2005-08-30 | 2008-07-23 | Bpw(梅州)车轴有限公司 | Heat treatment process for raising comprehensive performace of low alloy structure steel |
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