JPS63317623A - Production of wear resisting steel plate having excellent delayed cracking resistance - Google Patents
Production of wear resisting steel plate having excellent delayed cracking resistanceInfo
- Publication number
- JPS63317623A JPS63317623A JP15307587A JP15307587A JPS63317623A JP S63317623 A JPS63317623 A JP S63317623A JP 15307587 A JP15307587 A JP 15307587A JP 15307587 A JP15307587 A JP 15307587A JP S63317623 A JPS63317623 A JP S63317623A
- Authority
- JP
- Japan
- Prior art keywords
- cracking resistance
- delayed cracking
- temperature
- steel plate
- content
- 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 33
- 230000003111 delayed effect Effects 0.000 title claims abstract description 33
- 239000010959 steel Substances 0.000 title claims abstract description 33
- 238000005336 cracking Methods 0.000 title claims abstract description 32
- 238000004519 manufacturing process Methods 0.000 title claims description 18
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 10
- 238000005496 tempering Methods 0.000 claims abstract description 10
- 238000001816 cooling Methods 0.000 claims abstract description 6
- 238000005096 rolling process Methods 0.000 claims abstract description 6
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052742 iron Inorganic materials 0.000 claims abstract description 5
- 238000000034 method Methods 0.000 claims description 14
- 229910052748 manganese Inorganic materials 0.000 abstract description 6
- 229910052758 niobium Inorganic materials 0.000 abstract description 4
- 229910052720 vanadium Inorganic materials 0.000 abstract description 4
- 229910052804 chromium Inorganic materials 0.000 abstract description 3
- 238000010438 heat treatment Methods 0.000 abstract description 3
- 229910052802 copper Inorganic materials 0.000 abstract description 2
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 2
- 230000000694 effects Effects 0.000 description 17
- 230000007423 decrease Effects 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 4
- 239000010949 copper Substances 0.000 description 4
- 229920006395 saturated elastomer Polymers 0.000 description 3
- 238000005275 alloying Methods 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000005065 mining Methods 0.000 description 2
- 241000473391 Archosargus rhomboidalis Species 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 239000004744 fabric Substances 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 150000002431 hydrogen Chemical class 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 239000004576 sand Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000008399 tap water Substances 0.000 description 1
- 235000020679 tap water Nutrition 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野コ
本発明は耐遅れ割れ性の優れた耐摩耗用鋼板の製造方法
に関し、さらに詳しくは、鉱石や土砂による摩耗が問題
となる土木、鉱山機械のパケット、ダンプトラックの荷
台、ブルドーザ−の排土板等に使用される高硬度で、か
つ、耐遅れ割れ性の優れた耐摩耗用！４板の製造方法に
関する。[Detailed Description of the Invention] [Industrial Fields of Application] The present invention relates to a method for manufacturing a wear-resistant steel plate with excellent delayed cracking resistance, and more specifically, to civil engineering and mining machines where wear caused by ore and earth and sand is a problem. High hardness and wear resistance with excellent delayed cracking resistance, used for packets, dump truck beds, bulldozer earth removal plates, etc.! This invention relates to a method for manufacturing four plates.
［従来技術］
従来から、土木、鉱山機械等に使用される耐摩耗用鋼板
は、１００〜ｔ５０ｋｇｆ／龍２の高い強度を有するた
め、遅れ割れ感受性が高く、加工時に発生する微細な亀
裂或いはガス切断および溶接による熱影響部等の水素が
集積し易い場所を起点として、割れが発生するため加工
時に予熱、後熱等の煩雑な施行管理か必要となる。[Prior art] Wear-resistant steel plates conventionally used in civil engineering, mining machinery, etc. have a high strength of 100 to 50 kgf/Ryu2, and are therefore susceptible to delayed cracking, resulting in fine cracks or gas that occur during processing. Cracks occur in areas where hydrogen is likely to accumulate, such as the heat-affected zone caused by cutting and welding, and therefore require complicated implementation controls such as preheating and postheating during processing.
この耐遅れ割れ性を改善する方法としては、特開昭６０
−０５９０１９号公報に記載されているように、含有成
分のＭｎ含有量を低減することが有効であるが、Ｍｎの
低減による焼入れ性の低下を補うために、ＣｒおよびＭ
ｏ等の合金元素を多量に含有させる必要があり、製造コ
ストの上昇を招くのみならず、これらの元素が熱影響部
の硬さの上昇を招くため、遅れ割れを完全に防止するこ
とには、なお問題が残っていた。As a method for improving this delayed cracking resistance, JP-A-60
As described in Publication No. 059019, it is effective to reduce the Mn content of the contained components, but in order to compensate for the decrease in hardenability due to the reduction of Mn, Cr and Mn
It is necessary to contain large amounts of alloying elements such as o, which not only increases manufacturing costs, but also increases the hardness of the heat affected zone, so it is difficult to completely prevent delayed cracking. However, a problem remained.
［発明が解決しようとする問題点］
本発明は土足に説明したような従来技術の輝々の問題点
に鑑み、ＯｒおよびＭＯ等の合金元素を基本的に含有せ
ず、かつ、耐遅れ割れ性の優れた鋼を製造するために、
本発明者が鋭意研究を行ない、検討を重ね１こ結果、低
いＭｎ含有量による硬度低下を補うためには、微量のＮ
ｂを含有することか有効であること、また、微量のＴｉ
の含有か耐遅れ割れ性を向上させることを見出だし、耐
遅れ割れ性の優れた耐摩耗用鋼板の製造方法をｔａ＋発
しにのである。[Problems to be Solved by the Invention] In view of the bright problems of the prior art as explained in detail, the present invention basically does not contain alloying elements such as Or and MO, and has delayed cracking resistance. In order to produce superior steel,
The inventor of the present invention has conducted intensive research and has repeatedly considered1. As a result, in order to compensate for the decrease in hardness due to low Mn content, it is necessary to add a small amount of N.
It is effective to contain a small amount of Ti.
It was discovered that the inclusion of TA+ improves delayed cracking resistance, and a method for manufacturing a wear-resistant steel plate with excellent delayed cracking resistance was developed.
［問題点を解決するための手段］
本発明に係る耐遅れ割れ性の優れた耐摩耗用鋼板の製造
方法は、
（１）ＣＱ、１５〜０．３０ｗｔ％、Ｓｉ０．０５〜０
．８０ｗＬ％、Ｍｎ ０．５０〜０．８０ｗｔ％、Ａ
ｌ ０．Ｑｌ 〜０．０８ｗｔ％、Ｎｂ Ｑ、ＱＯ７〜
０．０２５ｗｔ％、Ｖ Ｑ、０２〜０．０８ｗｔ％、Ｔ
ｉ ０．（１０５〜０．０２５★ｔ％、Ｂ ０．０００
５〜０．００２５ｗｔ％を含有し、残部鉄および不可避
不純物よりなろ鋼スラブを１１００℃以上の温度に加熱
し、８００℃以上の温度で圧延を終了し、その後、直ち
に２００℃以下の温度まで急速冷却し、さらに、２００
〜５００℃の温度で焼戻すことを特徴とする耐遅れ割れ
性の優れた耐摩耗用鋼板の製造方法を第１の発明とし、
（２）Ｃ０．Ｌ５〜０．３Ｑｖ＋ｔ％、Ｓ Ｌ Ｑ、（
１５〜０．Ｂ（ｌｉｔ％、Ｍｎ ０．５０〜０．８０ｗ
ｔ％、Ａ ｌ ０．０１〜０．０８ｗｔ％、Ｎｂ ０．
００７〜０．０２５ｗｔ％、Ｖ ０．０２〜０．０８ｗ
ｔ％、Ｔｉ ０．００５〜０．０２５ｗｔ％、Ｂ ０．
（１（１０５〜０．（１０２５ｗｔ％を含有し、かつ、
Ｃｕ ０．ｌＱ 〜０．３０ｗｔ％、Ｃｒ ０．０５〜
０．２０ｗｔ％、Ｍｏ ０．０３〜０．１０ｗｔ％
の内から選んだ１種以上
を含有し、残部鉄および不可避不純物よりなろ鋼スラブ
を１１００°Ｃ以上の温度に加熱し、８００℃以上の温
度で圧延を終了し、その後、直ちに２００℃以下の温度
まで急速冷却し、さらに、２００〜５００℃の温度で焼
戻すことを特徴とする耐遅れ割れ性の優れた耐摩耗用ｗ
４板の製造方法を第２の発明とする２つの発明上りなる
ものである。[Means for Solving the Problems] The method for producing a wear-resistant steel plate with excellent delayed cracking resistance according to the present invention includes: (1) CQ, 15 to 0.30 wt%, Si 0.05 to 0;
．． 80wL%, Mn 0.50-0.80wt%, A
l 0. Ql ~0.08wt%, Nb Q, QO7~
0.025wt%, V Q, 02-0.08wt%, T
i0. (105~0.025★t%, B 0.000
A steel slab containing 5 to 0.0025 wt%, with the remainder iron and unavoidable impurities, is heated to a temperature of 1100°C or higher, finished rolling at a temperature of 800°C or higher, and then immediately rapidly reduced to a temperature of 200°C or lower. Cool, and then add 200
The first invention is a method for manufacturing a wear-resistant steel plate with excellent delayed cracking resistance, characterized by tempering at a temperature of ~500°C, (2) C0. L5~0.3Qv+t%, S L Q, (
15-0. B (lit%, Mn 0.50~0.80w
t%, Al 0.01-0.08wt%, Nb 0.
007~0.025wt%, V 0.02~0.08w
t%, Ti 0.005-0.025wt%, B 0.
(1(105~0.(1025 wt%), Cu 0.1Q~0.30 wt%, Cr 0.05~0.
0.20 wt%, Mo 0.03 to 0.10 wt%, and the remaining iron and unavoidable impurities are heated to a temperature of 1100°C or higher, Wear-resistant w with excellent delayed cracking resistance characterized by finishing rolling at a certain temperature, then immediately rapidly cooling to a temperature of 200°C or less, and further tempering at a temperature of 200 to 500°C.
This is a continuation of two inventions, with the second invention being a method for manufacturing four plates.
本発明に係る耐遅れ割れ性の優れた耐摩耗用鋼板の製造
方法について、以下詳細に説明する。The method for manufacturing a wear-resistant steel plate with excellent delayed cracking resistance according to the present invention will be described in detail below.
先ず、本発明に係る耐遅れ割れ性の優れた耐摩耗用Ｍ仮
の製造方法において使用する鋼板の含有成分および含有
割合について説明する。First, the components and content ratios of the steel plate used in the method for manufacturing a wear-resistant M temporary with excellent delayed cracking resistance according to the present invention will be explained.
Ｃは表面硬度を上昇させるのに極めて有効であり、ブリ
ネル硬さく）ＩＢ）３２１以上を確保するために必要な
元素であり、含有量が０．１５ｗｔ％未満では所要の硬
度が得られず、また、０゜３０ｗｔ％を越えて多量に含
有されると耐遅れ割れ性、溶接性が阻害される。よって
、Ｃ含有量は０．１５〜０．３０ｗｔ％とする。C is an element that is extremely effective in increasing surface hardness and is necessary to ensure Brinell hardness (IB) 321 or higher, and if the content is less than 0.15 wt%, the required hardness cannot be obtained. Furthermore, if the content exceeds 0.30 wt%, delayed cracking resistance and weldability will be impaired. Therefore, the C content is set to 0.15 to 0.30 wt%.
Ｓｔは脱酸に必要な元素であり、含有ｍが００５ｗｔ％
未満ではこの効果が少なく、また、０．８ｈＬ％を越え
ると溶接性を劣化させる。よって、Ｓｔ含有槓は０．０
５〜０．８０豐ｔ％とする。St is an element necessary for deoxidation, and the content m is 0.05 wt%
If it is less than 0.8hL%, this effect will be small, and if it exceeds 0.8hL%, weldability will deteriorate. Therefore, the St-containing shell is 0.0
5 to 0.80 t%.
Ｍｎは焼入れ性向上に有効な元素であり、含（ｆ虫が０
．５０ｗｔ％未満てはこの効果は少なく、また、０．８
０ｗｔ％を越えて含有されると遅れ割れ感受性を著しく
高める。よって、Ｍｎ含ｆＴｍは０．５０〜０３０ｗｔ
％とする。Mn is an effective element for improving hardenability, and the
．． This effect is small below 50 wt%, and 0.8
If the content exceeds 0 wt%, the susceptibility to delayed cracking increases significantly. Therefore, Mn-containing fTm is 0.50 to 030wt
%.
Ａｌは脱酸元素であり、含ｒｆ量が０．０１ｗｔ％未満
ではこの効果は少なく、また、０．０８ｗＬ％を越えて
含有されろと効果は飽和すると共に鋼の清浄度を悪化さ
せる。よって、Ａｔ含有爪は０．０１〜０．０８ｗｔ％
とする。Al is a deoxidizing element, and if the rf content is less than 0.01wt%, this effect is small, and if the content exceeds 0.08wL%, the effect is saturated and the cleanliness of the steel is deteriorated. Therefore, At-containing nails contain 0.01 to 0.08 wt%
shall be.
Ｎｂは２００〜５００℃の温度における低温焼戻し時の
銅板の表面硬度の低下を抑制する元素であり、含有量が
０．００７ｗｔ％未満ではこの効果は少なく、また、０
．０２５ｗｔ％を越えて含有されると効果は飽和する。Nb is an element that suppresses the decrease in surface hardness of a copper plate during low-temperature tempering at a temperature of 200 to 500 ° C. If the content is less than 0.007 wt%, this effect is small, and
．． When the content exceeds 0.025 wt%, the effect is saturated.
よって、Ｎｂ含有量は０．００７〜０．０２５ｗｔ％と
する。Therefore, the Nb content is set to 0.007 to 0.025 wt%.
■は少量で焼入れ性を高める元素であり、含有量が０．
０２ｗｔ％未満ではこのような効果を有効に発揮できず
、また、０．０８ｗｔ％を越えて含有されろと溶接性が
劣化する。よって、■含有量は０．０２〜０．０８ｗＬ
％とする。■ is an element that improves hardenability in small amounts, and its content is 0.
If the content is less than 0.02 wt%, such effects cannot be effectively exhibited, and if the content exceeds 0.08 wt%, weldability deteriorates. Therefore, ■The content is 0.02~0.08wL
%.
Ｔｉは炭窒化物を形成し、遅れ割れの原因となる水素の
トラップサイドとして作用し、耐遅れ割れ性の向上に有
効であり、含有量がＱ、００５ｗｔ５未満ではこの効果
が少なく、また、０．０２５ｗｊ％を越えて含有される
と効果は飽和してしまう。よって、Ｔｉ含含量量０．０
０５〜Ｑ、０２５ｗｔ％とする。Ti forms carbonitrides and acts as a trap side for hydrogen, which causes delayed cracking, and is effective in improving delayed cracking resistance.If the content is less than Q,005wt5, this effect is small; If the content exceeds .025wj%, the effect will be saturated. Therefore, the Ti content is 0.0
05 to Q, 025 wt%.
Ｂは微量の含有により綱の焼入れ性を高める元素であり
、含イイ量が０．（１００５★ｔ％未満ではこの効果を
有効に発揮することができず、また、０．００２５ｗｔ
％を越えて含有されるとその効果は消失するばかりか、
溶接性を劣化させろ。よ、って、Ｂ含有量は０．０ＯＱ
５〜０．００２５ｗｔ％とする。B is an element that improves the hardenability of the steel when contained in a trace amount, and the content is 0. (If it is less than 1005★t%, this effect cannot be exhibited effectively, and if it is less than 0.0025wt%,
If the content exceeds %, the effect not only disappears, but also
Deteriorate weldability. Yo, B content is 0.0OQ
5 to 0.0025 wt%.
また、上記の含有成分以外に、硬度水帛、板厚に応じて
ＣｕＳＣｒ、Ｍｏの内から選んだ１種以上を含有させる
ことができる。In addition to the above-mentioned components, one or more selected from CuSCr and Mo can be included depending on the hardness of the water fabric and the board thickness.
、Ｃｕは焼入れ性向上に有効な元素であり、含有量が０
．１０ｗｔ５未満ではこの効果を発揮することができず
、また、０．３０１℃％を越えて含有されると焼き割れ
が発生する。よって、Ｃｕ含有量は０．１０〜０．３Ｑ
ｗｔ％とする。, Cu is an effective element for improving hardenability, and the content is 0.
．． If the content is less than 10wt5, this effect cannot be exhibited, and if the content exceeds 0.301°C%, quench cracking will occur. Therefore, the Cu content is 0.10-0.3Q
Let it be wt%.
Ｃｒは焼入れ性向上に有効な元素であり、含有量が０．
０５ｗｔ％未満では効果を発揮することができず、また
、０．２０★ｔ％を越えて含有されると高価となる。よ
って、Ｃｒ含有量は０．０５〜０．２０ｗｔ％とする。Cr is an element effective in improving hardenability, and when the content is 0.
If the content is less than 0.05 wt%, the effect cannot be exhibited, and if the content exceeds 0.20★t%, it becomes expensive. Therefore, the Cr content is set to 0.05 to 0.20 wt%.
Ｍｏは焼入れ性を高め、かっ、焼戻し軟化抵抗を高める
元素であり、含有量が０．０３ｗｔ％未満ではこのよう
な効果を発揮できず、また、０ 、１０ｗｔ％を越えて
含有されると高価となる。よって、Ｍ。Mo is an element that increases hardenability and resistance to softening during tempering. If the content is less than 0.03 wt%, it cannot exhibit this effect, and if the content exceeds 0.10 wt%, it becomes expensive. becomes. Therefore, M.
含有量は０．０３〜０．１（１ｗｔ％とする。The content is 0.03 to 0.1 (1 wt%).
次に、本発明に係る耐遅れ割れ性の優れた耐摩耗用鋼板
の製造方法の製造条件について説明する。Next, the manufacturing conditions of the method for manufacturing a wear-resistant steel plate with excellent delayed cracking resistance according to the present invention will be explained.
加熱温度は、低温における焼戻しによる鋼板の表面硬度
の低下を抑制するＮｂの効果を有効に発揮させるため、
Ｎｂを充分に固溶させる必要があり、そのために加熱温
度は１１００℃以上とするのである。The heating temperature is set so that Nb effectively exhibits the effect of suppressing the decrease in surface hardness of the steel sheet due to tempering at low temperatures.
It is necessary to sufficiently dissolve Nb as a solid solution, and for this purpose, the heating temperature is set to 1100° C. or higher.
圧延仕上げ温度は、低くなると焼入れ性が低下するので
、８００℃以上とする。The rolling finish temperature is set to 800° C. or higher, since hardenability decreases as the temperature decreases.
冷却停止温度が高くなると、ａ＃ｆｔ、表面において完
全なマルテンサイト組織が得られにくくなるため、２０
０℃以下とする。As the cooling stop temperature increases, it becomes difficult to obtain a complete martensitic structure on the a#ft surface, so 20
The temperature shall be below 0℃.
冷却後の焼戻し温度は２００℃未満では閏坂内の残留応
力が大きく、加工性が劣化し、また、５００℃を越える
と表面の硬度が低下する。よりて、焼戻し温度は２００
〜５００℃とする。If the tempering temperature after cooling is less than 200°C, the residual stress within the slope will be large and the workability will deteriorate, and if it exceeds 500°C, the surface hardness will decrease. Therefore, the tempering temperature is 200
~500°C.
［実 施 例］
本発明に係る耐遅れ割れ性の優れた耐摩耗用鋼板の製造
方法の実施例を説明する。[Example] An example of the method for manufacturing a wear-resistant steel plate with excellent delayed cracking resistance according to the present invention will be described.
実施例１
第１表に示す含有成分および含有割合の鯛を通常の溶製
法により、溶解後鋳造し、その後、第２表に示す条件に
より鋼板を製造した。Example 1 A sea bream having the components and content ratios shown in Table 1 was melted and cast by a normal melting method, and then a steel plate was manufactured under the conditions shown in Table 2.
製造された鋼板の機械的性質を第２表に示す。Table 2 shows the mechanical properties of the manufactured steel sheets.
また、８０°Ｃの水道水中における低荷重引張試験（切
欠形状係数＝１０）による遅れ破壊強さを第１図に示す
。第１図において、１は本発明鋼、２は比較鋼を示す。Further, the delayed fracture strength obtained by a low-load tensile test (notch shape factor = 10) in tap water at 80°C is shown in Fig. 1. In FIG. 1, 1 indicates the steel of the present invention and 2 indicates the comparative steel.
本発明ａｔは比較Ｒ２に比較し、ＣｒｌＭｏを含有して
いないにも拘わらず、同等の機械的性質、表面ブリネル
硬さを有しており、また、耐遅れ割れ性は優れている。Compared to Comparative R2, at of the present invention has similar mechanical properties and surface Brinell hardness, and is superior in delayed cracking resistance, even though it does not contain CrlMo.
実施例２
第３表に示す含有成分および含ａ割合の鋼を通常の溶製
法により溶解し、鋳造後、第４表に示す条件により製造
した。Example 2 Steel having the components and a content ratio shown in Table 3 was melted by a normal melting method, and after casting, it was manufactured under the conditions shown in Table 4.
製造されたＭ仮の、表面ブリネル硬さ、遅れ破壊強さを
第４表に示す。Table 4 shows the surface Brinell hardness and delayed fracture strength of the manufactured M temporary.
本発明に係る耐遅れ割れ性の優れた耐摩耗用鋼板の製造
方法により製造された鋼板のＡ−Ｆは、いずれも高い表
面ブリネル硬さと優れた耐遅れ割れ性を示しているのに
対し、比較ｊＩ＋１１ＧはＮｂを含有していないため硬
度が低く、比較Ｎ４１−（はＮｂを含有しているので硬
度は高いが、Ｔｉを含イイしないため耐遅れ割れ性は劣
り、また、比較ＸＪ４１はＮｂおよびＴｉを含す■して
いないので硬度および耐遅れ割れ性のいずれも劣ってい
ることがわかる。Steel plates A-F manufactured by the method of manufacturing a wear-resistant steel plate with excellent delayed cracking resistance according to the present invention all exhibit high surface Brinell hardness and excellent delayed cracking resistance. Comparison jI+11G has low hardness because it does not contain Nb, comparative N41-( has high hardness because it contains Nb, but has poor delayed cracking resistance because it does not contain Ti, and comparative XJ41 has Nb It can be seen that both the hardness and the delayed cracking resistance are poor since the sample (1) does not contain Ti.
［発明の効果］
以上説明したように、本発明に係る耐遅れ割れ性の優れ
た耐摩耗用鋼板の製造方法は上記の構成であるから、表
面硬度および耐遅れ割れ性に優れた鋼板を効率よく製造
することができろという効果を何するものである。[Effects of the Invention] As explained above, since the method for manufacturing a wear-resistant steel plate with excellent delayed cracking resistance according to the present invention has the above configuration, it is possible to efficiently produce a steel plate with excellent surface hardness and delayed cracking resistance. What is the effect of being able to manufacture it well?
第１図は負荷応力と破断までの時間との関係を示す図で
ある。FIG. 1 is a diagram showing the relationship between applied stress and time until breakage.
Claims (2)
．８０ｗｔ％、Ｍｎ０．５０〜０．８０ｗｔ％、Ａｌ０
．０１〜０．０８ｗｔ％、Ｎｂ０．００７〜０．０２５
ｗｔ％、Ｖ０．０２〜０．０８ｗｔ％、Ｔｉ０．００５
〜０．０２５ｗｔ％、 Ｂ０．０００５〜０．００２５ｗｔ％ を含有し、残部鉄および不可避不純物よりなる鋼スラブ
を１１００℃以上の温度に加熱し、８００℃以上の温度
で圧延を終了し、その後、直ちに２００℃以下の温度ま
で急速冷却し、さらに、２００〜５００℃の温度で焼戻
すことを特徴とする耐遅れ割れ性の優れた耐摩耗用鋼板
の製造方法。(1) C0.15-0.30wt%, Si0.05-0
．． 80wt%, Mn0.50-0.80wt%, Al0
．． 01-0.08wt%, Nb0.007-0.025
wt%, V0.02-0.08wt%, Ti0.005
A steel slab containing ~0.025wt%, B0.0005~0.0025wt%, and the balance consisting of iron and unavoidable impurities is heated to a temperature of 1100°C or higher, and rolling is finished at a temperature of 800°C or higher, and then, A method for producing a wear-resistant steel plate with excellent delayed cracking resistance, characterized by immediately rapid cooling to a temperature of 200°C or less, and further tempering at a temperature of 200 to 500°C.
．８０ｗｔ％、Ｍｎ０．５０〜０．８０ｗｔ％、Ａｌ０
．０１〜０．０８ｗｔ％、Ｎｂ０．００７〜０．０２５
ｗｔ％、Ｖ０．０２〜０．０８ｗｔ％、Ｔｉ０．００５
〜０．０２５ｗｔ％、 Ｂ０．０００５〜０．００２５ｗｔ％ を含有し、かつ、 Ｃｕ０．１０〜０．３０ｗｔ％、Ｃｒ０．０５〜０．２
０ｗｔ％、Ｍｏ０．０３〜０．１０ｗｔ％ の内から選んだ１種以上 を含有し、残部鉄および不可避不純物よりなる鋼スラブ
を１１００℃以上の温度に加熱し、８００℃以上の温度
で圧延を終了し、その後、直ちに２００℃以下の温度ま
で急速冷却し、さらに、２００〜５００℃の温度で焼戻
すことを特徴とする耐遅れ割れ性の優れた耐摩耗用鋼板
の製造方法。(2) C0.15-0.30wt%, Si0.05-0
．． 80wt%, Mn0.50-0.80wt%, Al0
．． 01-0.08wt%, Nb0.007-0.025
wt%, V0.02-0.08wt%, Ti0.005
~0.025wt%, B0.0005~0.0025wt%, and Cu0.10~0.30wt%, Cr0.05~0.2
A steel slab containing one or more selected from 0wt%, Mo0.03 to 0.10wt%, and the balance consisting of iron and unavoidable impurities is heated to a temperature of 1100°C or higher, and then rolled at a temperature of 800°C or higher. A method for manufacturing a wear-resistant steel plate with excellent delayed cracking resistance, characterized by immediately cooling rapidly to a temperature of 200°C or less, and then tempering at a temperature of 200 to 500°C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15307587A JPS63317623A (en) | 1987-06-19 | 1987-06-19 | Production of wear resisting steel plate having excellent delayed cracking resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15307587A JPS63317623A (en) | 1987-06-19 | 1987-06-19 | Production of wear resisting steel plate having excellent delayed cracking resistance |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS63317623A true JPS63317623A (en) | 1988-12-26 |
Family
ID=15554428
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP15307587A Pending JPS63317623A (en) | 1987-06-19 | 1987-06-19 | Production of wear resisting steel plate having excellent delayed cracking resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS63317623A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US8097099B2 (en) | 2005-09-09 | 2012-01-17 | Nippon Steel Corporation | High toughness abrasion resistant steel with little change in hardness during use and method of production of same |
| CN103397272A (en) * | 2013-07-29 | 2013-11-20 | 莱芜钢铁集团有限公司 | Abrasion-resistant steel plate with low crack sensitive index and high strength and preparation method thereof |
| WO2015115086A1 (en) | 2014-01-28 | 2015-08-06 | Ｊｆｅスチール株式会社 | Wear-resistant steel plate and process for producing same |
-
1987
- 1987-06-19 JP JP15307587A patent/JPS63317623A/en active Pending
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US8097099B2 (en) | 2005-09-09 | 2012-01-17 | Nippon Steel Corporation | High toughness abrasion resistant steel with little change in hardness during use and method of production of same |
| CN103397272A (en) * | 2013-07-29 | 2013-11-20 | 莱芜钢铁集团有限公司 | Abrasion-resistant steel plate with low crack sensitive index and high strength and preparation method thereof |
| CN103397272B (en) * | 2013-07-29 | 2015-12-09 | 莱芜钢铁集团有限公司 | There is wear-resisting steel plate of low crack-sensitivity exponential sum high strength and preparation method thereof |
| WO2015115086A1 (en) | 2014-01-28 | 2015-08-06 | Ｊｆｅスチール株式会社 | Wear-resistant steel plate and process for producing same |
| KR20160113683A (en) | 2014-01-28 | 2016-09-30 | 제이에프이 스틸 가부시키가이샤 | Wear-resistant steel plate and process for producing same |
| US10662493B2 (en) | 2014-01-28 | 2020-05-26 | Jfe Steel Corporation | Abrasion-resistant steel plate and method for manufacturing the same |
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