JPH06287638A - Production of wear resistant bar steel - Google Patents
Production of wear resistant bar steelInfo
- Publication number
- JPH06287638A JPH06287638A JP10044693A JP10044693A JPH06287638A JP H06287638 A JPH06287638 A JP H06287638A JP 10044693 A JP10044693 A JP 10044693A JP 10044693 A JP10044693 A JP 10044693A JP H06287638 A JPH06287638 A JP H06287638A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- wear resistance
- temperature
- bar
- rolling
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
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- Heat Treatment Of Steel (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は岩石粉砕用機械やブルド
−ザ−等の建設機械の各種部材として使用されるのに適
した耐摩耗性棒鋼の製造方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a wear-resistant steel bar suitable for being used as various members of rock crushing machines and construction machines such as bulldozers.
【０００２】[0002]
【従来の技術及びその技術的課題】ブルド−ザ−等で代
表される建設機械や岩石粉砕用機械を構成する各種部材
は、用途上、土砂、砂利、コンクリ−ト、岩石に対する
十分な耐摩耗性が要求される。一般に耐摩耗性を向上さ
せるためには、部材の素材としての棒鋼の硬度を上昇さ
せることが重要であり、このため圧延後の棒鋼に焼入れ
焼戻し(調質)あるいは高周波焼入れを施して所望の硬度
としてきた。しかし、調質処理は焼入れのために一度オ
−ステナイト域の温度にまで再加熱せねばならず、また
焼戻しのため500℃付近に1〜2時間加熱保持せねばなら
ないため、多大なコストの上昇を招いていた。また、高
周波焼入れにおいても、仕掛かり品およびコストの増加
という同様の問題を有していた。2. Description of the Related Art Various members constituting construction machines and rock crushing machines represented by bulldozers and the like have a sufficient wear resistance to earth and sand, gravel, concrete and rocks in terms of use. Sex is required. In general, in order to improve wear resistance, it is important to increase the hardness of the steel bar as a material of the member.Therefore, the steel bar after rolling is subjected to quenching and tempering (tempering) or induction hardening to obtain the desired hardness. I've been. However, the tempering treatment must be reheated once to the temperature of the austenite region for quenching, and it must be heated and held at around 500 ° C for 1 to 2 hours for tempering. Was invited. Further, in induction hardening, there is a similar problem that the work in process and the cost increase.
【０００３】近年、調質処理を省略するため、特開昭６
０−１４１８３２公報、特開昭６４−３１９２８公報の
ように、熱間圧延における熱を利用して棒鋼に直接焼入
れを施し、さらに内部保有熱により自己焼戻しを施すい
わゆる直接焼入れ法が開発されている。しかしながらこ
の方法を高周波焼入れと比較した場合、高周焼入れ材の
焼戻し温度は通常150から200℃の低温であるのに対し、
直接焼入れにおける自己焼戻し温度は通常500から600℃
で、低くしても300℃が限界である。このため直接焼入
れ法では、マルテンサイトの焼戻しが過度に進んでしま
い、とても高周波焼入れ材に匹敵する硬度を得ることが
できず、直接焼入れ法によって製造された棒鋼は高周波
焼入れ材より耐摩耗性が劣っているという欠点を有して
いた。In recent years, in order to omit the refining process, Japanese Patent Laid-Open No.
A so-called direct quenching method has been developed, such as 0-141832 and Japanese Patent Laid-Open No. 64-31928, in which the steel bar is directly quenched using the heat of hot rolling and further self-tempered by the internal heat. . However, when this method is compared with induction hardening, the tempering temperature of high-peripheral quenching materials is usually as low as 150 to 200 ° C.
Self tempering temperature in direct quenching is usually 500 to 600 ℃
And, even if it is lowered, the limit is 300 ℃. Therefore, in the direct quenching method, the tempering of martensite proceeds excessively, and it is not possible to obtain a hardness that is very comparable to that of the induction hardened material. It had the disadvantage of being inferior.
【０００４】本発明は前記のような問題点を解消するた
めに創案されたもので、その目的とするところは、直接
焼入れ法の利点を生かしつつ弱点であった硬度不足を解
消し、耐摩耗性を飛躍的に向上させることができる棒鋼
の製造方法を提供することにある。The present invention was devised to solve the above-mentioned problems, and its purpose is to eliminate the lack of hardness, which was a weak point, while taking advantage of the advantages of the direct quenching method, and to improve wear resistance. An object of the present invention is to provide a method for manufacturing a steel bar capable of dramatically improving the property.
【０００５】[0005]
【課題を解決するための手段】上記目的を達成するため
本発明者らは実験と研究を重ね、直接焼き入れと鋼の成
分組成を組合せ、焼戻しマルテンサイト層に硬質炭化
物、窒化物を分散させると耐摩耗性が飛躍的に向上し、
高周波焼入れ材に勝るとも劣らない性能になることを見
い出し本発明に到った。すなわち、本発明は、重量％
で、C：O.30〜1.10%、Si:0.1〜1.8%、Mn:0.5〜2.0% Sol
Al:0.05〜0.1%、N:0.005〜0.03%でTi、Zr、Nb、Vのう
ちの1種または2種以上を0.1〜1.0%含有し、残部不可避
的に混入する元素と鉄よりなる鋼片を熱間圧延に際し
て、Ac3〜1050℃の間の温度で仕上げ圧延を行った後、
鋼材表面を強制冷却によりMs点以下に急冷して後、鋼材
内部の保有熱により300〜700℃の間の温度に自己焼戻し
させて、表層部に焼戻しマルテンサイトと硬質炭化物を
有する組織を得ることを特徴とするする。また、本発明
は、前記成分組成に加え、Ni：O.1〜1.0%、Cr：0.1〜1.
5%、Mo:O.05〜0.5%、B:O.0005〜0.0050%のうちの少なく
とも1種を含有し、残部不可避的に混入する元素と鉄よ
りなる鋼片を使用することを含む。さらに、前記いずれ
の発明においても、S:0.01〜0.10%、Pb:0.03〜0.30%、B
i:0.03〜0.30%、Se:0.01〜0.10%、Te:0.01〜0.10%、Ca:
0.001〜0.010%のうちの1種または2種以上を含有するも
のを含む。[Means for Solving the Problems] In order to achieve the above object, the present inventors have conducted experiments and researches and have combined direct quenching and composition of steel to disperse hard carbides and nitrides in a tempered martensite layer. And wear resistance has improved dramatically,
The inventors have found that the performance is not inferior to that of the induction hardened material, and arrived at the present invention. That is, the present invention is
, C: O.30 to 1.10%, Si: 0.1 to 1.8%, Mn: 0.5 to 2.0% Sol
Steel consisting of Al and 0.05 to 0.1%, N: 0.005 to 0.03%, 0.1 to 1.0% of one or more of Ti, Zr, Nb, and V, with the balance being elements inevitably mixed with iron. Upon hot rolling the piece, after finish rolling at a temperature between Ac 3 and 1050 ° C.,
To obtain a structure with tempered martensite and hard carbide in the surface layer by quenching the surface of the steel material below the Ms point by forced cooling and then self-tempering to a temperature between 300 and 700 ° C by the heat retained inside the steel material. Is characterized by. Further, the present invention, in addition to the above component composition, Ni: O.1 to 1.0%, Cr: 0.1 to 1.
5%, Mo: O.05 to 0.5%, B: O.0005 to 0.0050%, and the use of a steel slab composed of iron and an element that is unavoidably mixed with the balance. Furthermore, in any of the above inventions, S: 0.01 to 0.10%, Pb: 0.03 to 0.30%, B
i: 0.03-0.30%, Se: 0.01-0.10%, Te: 0.01-0.10%, Ca:
Including those containing one or more of 0.001 to 0.010%.
【０００６】[0006]
【作用】以下本発明を詳細に説明する。まず、本発明に
おいて使用する鋼の成分限定理由について説明する。 ・C：0.30〜1.10％ Cは鋼の強度ならびに硬質炭化物の分散による耐摩耗性
を確保するのに重要な元素であるが、0.30%未満では焼
入れ時のマルテンサイトの硬度が十分でないので、0.30
%以上添加する必要がある。しかし、1.10%を越えて添加
しても硬度ならびに耐摩耗性の向上は顕著ではなく、ま
た、靱性の低下が大きくなるので0.30〜1.10%の間とす
る。 ・Si:0.1〜1.8％ Siは脱酸剤として重要であり、またフェライトに固溶し
て鋼を強化する。このためには0.1%以上添加する必要が
あるが、1.8%を越えると鋼の清浄性を低下し靱性を劣化
させる。また、脱炭が大きくなるので0.1〜1.8%の間と
する。 ・Mn：0.5〜2.0％ Mnは焼き入れ性を高め、鋼を強靱化するのに有効な元素
である。0.5%未満では所望の強靱性を有する鋼を得るこ
とが困難である。しかし、2.0%を越えて添加かしてもベ
イナイトの占める割合を高くしてかえって靱性を損なう
ことになるので0.5〜2.0%の間とする。・ Sol Ａｌ:0.05〜0.1％ Alは脱酸剤として必要であり、また、Nと結合してAlNを
生成し、結晶粒を微細化させ、靱性、疲労強度を向上さ
せるのに有効な元素である。このためには、0.05 Sol A
l%以上添加する必要があるが、0.1 Sol Al%を越えると
アルミナ系介在物が増加し靱性を劣化させるので0.05〜
0.1 Sol Al%の間とする。 ・N：0.005〜0.03％ Nは結晶粒微細化ならびに硬質窒化物の分散による耐摩
耗性の向上に重要な元素であるが、0.005%未満ではその
効果は少なく、一方、0.03%を越えると過剰な窒素がフ
ェライトに固溶して延性を低下する。また、加工中にひ
ずみ時効を起こして加工性を低下させるので0.005〜0.0
3%の間とする。The present invention will be described in detail below. First, the reasons for limiting the components of the steel used in the present invention will be described.・ C: 0.30 to 1.10% C is an important element for securing the strength of steel and wear resistance due to dispersion of hard carbides, but if it is less than 0.30%, the hardness of martensite during quenching is insufficient, so 0.30
% Or more must be added. However, even if added in excess of 1.10%, the hardness and wear resistance are not significantly improved, and the toughness decreases significantly, so the content is made 0.30 to 1.10%.・ Si: 0.1-1.8% Si is important as a deoxidizer, and solid-solves with ferrite to strengthen steel. For this purpose, it is necessary to add 0.1% or more, but if it exceeds 1.8%, the cleanliness of the steel decreases and the toughness deteriorates. In addition, decarburization becomes large, so 0.1 to 1.8% is set. -Mn: 0.5 to 2.0% Mn is an element effective in enhancing hardenability and strengthening steel. If it is less than 0.5%, it is difficult to obtain a steel having a desired toughness. However, even if added over 2.0%, the proportion occupied by bainite will be increased and the toughness will be impaired, so the content is made 0.5 to 2.0%.・ Sol Al: 0.05-0.1% Al is necessary as a deoxidizing agent, and is an element effective in improving the toughness and fatigue strength by combining with N to generate AlN, refining the crystal grains. is there. For this, 0.05 Sol A
It is necessary to add 1% or more, but if 0.1 Sol Al% is exceeded, alumina inclusions increase and the toughness deteriorates.
It should be between 0.1 Sol Al%. -N: 0.005 to 0.03% N is an important element for improving the wear resistance by refining the crystal grains and dispersing hard nitrides, but if less than 0.005%, its effect is small, while if it exceeds 0.03%, it is excessive. Nitrogen forms a solid solution with ferrite and reduces ductility. In addition, strain aging during processing reduces workability, so 0.005 to 0.0
Set between 3%.
【０００７】・Ti、Zr、Nb、Vのうちの１種または２種
以上：0.1〜1.0％ Ti、Zr、Nb、ならびにVは硬質炭化物、窒化物の分散に
よる耐摩耗性の向上に重要な元素である。このために
は、0.1%以上添加する必要があるが、1.0%を越えて添加
しても効果は飽和するのみならず、靱性を劣化させるた
め0.1〜1.0%の間とする。 ・Ni：0.1〜1.0％、Cr：0.1〜1.5％、Mo：0.05〜0.5
％、B：0.0005〜0.0050％のうちの少なくとも１種 Ni、Cr、MoならびにBは鋼の焼入れ性を向上させる元素
であり、焼入れ焼戻しにより所望の強度を得る時に添加
される。しかしながら、その添加量がNi 0.1%未満、Cr
0.1%未満、Mo 0.05%未満、B 0.0005%未満では、焼入れ
性向上の効果は小さい。一方、Ni 1.0%、Cr 1.5%、Mo
0.5%、B 0.0050%を越えて添加すると、圧延後に内部に
ベイナイトが出やすくなって靱性を劣化させるため、N
i：0.1〜1.0%、Cr：0.1〜1.5%、Mo：0.05〜0.5%、B：0.
0005〜0.0050%の間とする。 ・S：0.01〜0.10％、Pb：0.03〜0.30％、Bi：0.03〜0.3
0％、Se：0.01〜0.10％、Te：0.01〜0.10％、Ca：0.001
〜0.010％のうちの１種または２種以上 S、Pb、Bi、Se、TeならびにCaは切削性が重視される場
合に添加される。しかしながら、その添加量が、S 0.01
%未満、Pb 0.03%未満、Bi 0.03%未満、Se 0.01%未満、T
e 0.01%未満、Ca 0.001%未満では切削性への寄与が小さ
い。一方、S 0.01%、Pb 0.30%、Bi 0.30%、Se 0.10%、T
e0.10%、Ca 0.010%を越えて添加しても効果が飽和して
しまい、また経済的にも不利であるため、これらの元素
はS：0.01〜0.10%、Pb：0.03〜0.30%、Bi：0.03〜0.30
%、Se：0.01〜0.10%、Te：0.01〜0.10%、Ca：0.001〜0.
010%の間とする。 以上の元素の他に鋼はP、Cu等の不可避的に混入する元
素を含む。One or more of Ti, Zr, Nb, and V: 0.1 to 1.0% Ti, Zr, Nb, and V are important for improving wear resistance by dispersing hard carbides and nitrides. It is an element. For this purpose, it is necessary to add 0.1% or more, but if it is added over 1.0%, not only the effect is saturated but also the toughness is deteriorated, so the content is made 0.1 to 1.0%.・ Ni: 0.1-1.0%, Cr: 0.1-1.5%, Mo: 0.05-0.5
%, B: 0.0005 to 0.0050% of at least one element Ni, Cr, Mo and B are elements that improve the hardenability of steel, and are added when the desired strength is obtained by quenching and tempering. However, the addition amount is less than 0.1% Ni, Cr
If it is less than 0.1%, Mo is less than 0.05%, and B is less than 0.0005%, the effect of improving hardenability is small. On the other hand, Ni 1.0%, Cr 1.5%, Mo
If added in excess of 0.5% and B 0.0050%, bainite is likely to appear in the inside after rolling, which deteriorates toughness.
i: 0.1 to 1.0%, Cr: 0.1 to 1.5%, Mo: 0.05 to 0.5%, B: 0.
It is set between 0005 and 0.0050%.・ S: 0.01 to 0.10%, Pb: 0.03 to 0.30%, Bi: 0.03 to 0.3
0%, Se: 0.01 to 0.10%, Te: 0.01 to 0.10%, Ca: 0.001
One or more of 0.010% to S, Pb, Bi, Se, Te and Ca are added when machinability is important. However, the addition amount is S 0.01
%, Pb less than 0.03%, Bi less than 0.03%, Se less than 0.01%, T
If it is less than 0.01% and Ca is less than 0.001%, the contribution to machinability is small. On the other hand, S 0.01%, Pb 0.30%, Bi 0.30%, Se 0.10%, T
Since the effect is saturated even if added over 0.10% and Ca 0.010%, and it is economically disadvantageous, these elements are S: 0.01 to 0.10%, Pb: 0.03 to 0.30%, Bi: 0.03-0.30
%, Se: 0.01 to 0.10%, Te: 0.01 to 0.10%, Ca: 0.001 to 0.
It is between 010%. In addition to the above elements, steel contains elements such as P and Cu that are inevitably mixed.
【０００８】本発明は上記成分の鋼を熱間圧延し、圧延
直後に直接焼き入れを施し、表層部に焼戻しマルテンサ
イトと硬質炭化物を有する組織を得る。この場合の仕上
げ圧延温度、急冷温度及び自己焼戻し温度の限定理由は
以下のとおりである。 ・仕上げ圧延温度：Ac3変態点〜1050℃ 仕上げ圧延終了温度がAc3未満ではマルテンサイト単層
を得ることができず、また、圧延機にかかる負荷が大き
くなりすぎると同時に、表面疵の発生が著しくなる。一
方、1050℃を越えると圧延中の動的再結晶および圧延後
の静的結晶の進行が著しく、微細な結晶粒を得ることが
できず、靱性が低下するのでAc3〜1050℃の間とする。 ・仕上げ圧延後急冷時の鋼の表面温度：Ｍｓ点以下 急冷時の鋼の表面温度がMs点より高い場合はマルテンサ
イトを得ることができないのでMs点以下に急冷する必要
がある。急冷には一般に水を用いる。 ・復熱後の表面温度：300〜700℃ 急冷により得られたマルテンサイトはそのままでは靱性
に欠ける。また、焼入れ歪を開放して棒の曲がりを防止
するために焼戻す必要がある。300℃未満の復熱では焼
戻しが不十分で棒の曲がりを防止できない。一方、700
℃を越える復熱ではマルテンサイトの分解が速く十分硬
化した表層を得ることができないので復熱の温度は300
〜700℃の間とする。According to the present invention, the steel having the above components is hot-rolled and directly quenched immediately after rolling to obtain a structure having tempered martensite and hard carbide in the surface layer portion. The reasons for limiting the finish rolling temperature, the quenching temperature and the self tempering temperature in this case are as follows. -Finishing rolling temperature: Ac 3 transformation point to 1050 ° C If the finishing rolling ending temperature is less than Ac 3 , a martensite single layer cannot be obtained, and the load applied to the rolling mill becomes too large, and at the same time surface defects occur. Becomes noticeable. On the other hand, when the temperature exceeds 1050 ° C, the progress of dynamic recrystallization during rolling and the progress of static crystal after rolling is remarkable, and it is not possible to obtain fine crystal grains, and the toughness decreases, so between Ac 3 and 1050 ° C. To do. -Steel surface temperature during quenching after finish rolling: Ms point or lower If the surface temperature of the steel during quenching is higher than the Ms point, martensite cannot be obtained, so it is necessary to quench the temperature to the Ms point or lower. Water is generally used for quenching.・ Surface temperature after recuperation: 300-700 ℃ Martensite obtained by rapid cooling lacks toughness as it is. Further, tempering is necessary to release quenching distortion and prevent bending of the rod. When recuperated below 300 ° C, tempering is insufficient and bending of the bar cannot be prevented. On the other hand, 700
With recuperation exceeding ℃, the decomposition temperature of martensite is fast and a fully hardened surface layer cannot be obtained.
Between ~ 700 ℃.
【０００９】[0009]
【実施例】以下本発明を実施例に従って詳細に説明す
る。まず、試験に用いた供試材の化学成分を表１に示
す。表１中の鋼Ａは0.64%C-0.29%Si-1,58%Mnで、硬質炭
化物生成元素としてTiを含む鋼である。鋼Ｂは0.65%C-
1.22%Si-0.61%Mnで、硬質炭化物生成元素としてTi、Z
r、Nb、V、焼入れ性向上元素としてCr、B、切削性向上
元素としてPb、Caを含む鋼である。鋼Ｃは0.84%C-0.31%
Si-1.19%Mnで、硬質炭化物生成元素としてTi、Vを含む
鋼であり、鋼Ｄは通常のSMn443である。EXAMPLES The present invention will be described in detail below with reference to examples. First, Table 1 shows the chemical components of the test materials used in the test. Steel A in Table 1 is a steel containing 0.64% C-0.29% Si-1,58% Mn and containing Ti as a hard carbide forming element. Steel B is 0.65% C-
1.22% Si-0.61% Mn, Ti, Z as hard carbide forming elements
Steel containing r, Nb, V, hardenability improving elements Cr, B, and machinability improving elements Pb, Ca. Steel C is 0.84% C-0.31%
It is a steel containing Si-1.19% Mn and containing Ti and V as hard carbide forming elements, and Steel D is ordinary SMn443.
【００１０】[0010]
【表１】 [Table 1]
【００１１】表２に試験条件を、表３に試験結果を示
す。なお、表２の熱処理条件ｄにおける圧延−冷却中の
鋼材表面温度変化を示すと図１の通りであり、図１にお
いて１は加熱炉、２は圧延機群、３は水冷帯、４は冷却
床である。表３において、硬さはHV、YS,TSの単位はKgf
/mm2、El,RAの単位は％である。また、表層部組織の符
号に関し、T.Mは焼戻しマルテンサイト、Fはフェライ
ト、Pはパーライト、Bはベイナイトを示す。耐摩耗性比
は試験No.8の摩耗量を１として耐摩耗性を比で示したも
のであり、耐摩耗性の試験はラバーホイール摩耗試験装
置で実施した。図２はこの試験方法を模式的に示してお
り、試験片７を揺動腕５に取付け、おもり８により試験
片７を回転するラバーホール６に押しつけつつ上方から
摩耗剤９を散布したものである。試験条件は、ホイール
回転速度:150rpm、荷重:15Kgf、延べ回転数:5000回、摩
耗剤成分:100%SiO2である。Table 2 shows the test conditions, and Table 3 shows the test results. The change in steel surface temperature during rolling-cooling under heat treatment condition d in Table 2 is as shown in FIG. 1. In FIG. 1, 1 is a heating furnace, 2 is a rolling mill group, 3 is a water cooling zone, and 4 is cooling. On the floor. In Table 3, hardness is HV, YS, TS units are Kgf
The unit of / mm 2 and El, RA is%. Regarding the sign of the surface layer structure, TM indicates tempered martensite, F indicates ferrite, P indicates pearlite, and B indicates bainite. The wear resistance ratio is a ratio of the wear resistance of Test No. 8 with the wear amount being set to 1, and the wear resistance test was carried out by a rubber wheel wear tester. FIG. 2 schematically shows this test method, in which the test piece 7 is attached to the swing arm 5, and the wear agent 9 is sprayed from above while the test piece 7 is pressed against the rotating rubber hole 6 by the weight 8. is there. The test conditions are: wheel rotation speed: 150 rpm, load: 15 Kgf, total rotation speed: 5000 times, and abrasive component: 100% SiO 2 .
【００１２】[0012]
【表２】 [Table 2]
【００１３】[0013]
【表３】 [Table 3]
【００１４】試験結果を表３の試験No.に従って説明す
る。No.１〜４は鋼Ａ、No.５は鋼Ｄを用いたφ50mmにつ
いての結果である。 No.１：最終圧延後、水冷を行わない通常圧延の例であ
るが、組織はフェライト＋パ−ライトとなっており、N
o.５のSMn443オフライン高周波焼入れ材と比較すると、
表面硬度が低く、耐摩耗性が劣っている。 No.２：やや高めの温度で最終圧延した後、水冷した例
であるが、水冷後の表面温度がMs点より高いため、No.
１と同じ程度の結果しか得られていない。 No.３：水冷後の表面温度をNo.２より低いMs点以下とし
た例であるが、表面硬度が高く耐摩耗性に優れている。
また、内部組織は少量のベイナイトと微細なフェライト
＋パ−ライトよりなる組織で、良好な強靱性を有する。 No.４：No.３より低い最終圧延温度としたため、粒が微
細化してフェライトが出やすくなったことによりわずか
に強度は低下しているが、靱性はNo.３よりさらに良好
である。表面硬度はNo.３と同様に高硬度であり、良好
な耐摩耗性を有している。 No.５：SMn443のオフライン高周波焼入れ材の例であ
る。The test results will be described according to the test No. in Table 3. Nos. 1 to 4 are results for φ50 mm using steel A and No. 5 is for steel D. No. 1: This is an example of normal rolling without water cooling after the final rolling, but the structure is ferrite + pearlite, and N
Compared with the SMn443 offline induction hardened material of o.5,
Low surface hardness and poor wear resistance. No. 2: This is an example of water cooling after final rolling at a slightly higher temperature, but since the surface temperature after water cooling is higher than the Ms point, No.
Only the same result as 1 was obtained. No. 3: It is an example in which the surface temperature after water cooling is set to the Ms point lower than that of No. 2 or less, but the surface hardness is high and the wear resistance is excellent.
The internal structure is a structure composed of a small amount of bainite and fine ferrite + pearlite, and has good toughness. No. 4: Since the final rolling temperature was lower than that of No. 3, the strength was slightly decreased due to the grain refinement and the easy occurrence of ferrite, but the toughness was even better than No. 3. The surface hardness is as high as No. 3 and has good wear resistance. No. 5: It is an example of the offline induction hardening material of SMn443.
【００１５】No.６は鋼Ｂ、No.７は鋼Ｃ、No.８は鋼Ｄ
を用いてφ50mm棒鋼に熱処理条件ｄを適用して試験した
例である。 No.６：Mn量を低くしても、Si、Cr、Bの増加、添加によ
り良好な耐摩耗性を示している。 No.７：高C-高Ti、Vのため高い耐摩耗性を示している。 No.８：SMn443に本圧延−冷却方法を適用した例であ
り、この場合の摩耗量を1として耐摩耗性評価の基準と
した。 以上の試験結果から、本発明で規定した成分組成と熱処
理条件により、従来のオフライン高周波焼入れ材と同等
の優れた耐摩耗性を有する直接調質棒鋼の製造が可能と
なることがわかる。No. 6 is steel B, No. 7 is steel C, No. 8 is steel D
This is an example of a test in which a heat treatment condition d is applied to a φ50 mm steel bar using. No. 6: Even if the amount of Mn is reduced, good wear resistance is exhibited by increasing and adding Si, Cr, and B. No. 7: High C-high Ti and V show high wear resistance. No. 8: This is an example in which the present rolling-cooling method was applied to SMn443, and the wear amount in this case was set as 1 and used as the standard for evaluation of wear resistance. From the above test results, it is understood that it is possible to produce a direct tempered steel bar having excellent wear resistance equivalent to that of the conventional off-line induction hardened material by the composition of components and heat treatment conditions specified in the present invention.
【００１６】[0016]
【発明の効果】以上説明した本発明によるときには、所
定成分の鋼を圧延し、圧延直後の棒鋼に所定条件で直接
焼入れを施して表面を硬質炭化物を有する焼戻しマルテ
ンサイト組織とするため、オフライン高周波焼入れ材と
同等の優れた耐摩耗性を有する棒鋼をオンライン上で得
ることができ、岩石粉砕用機械や建設機械の各種部材の
加工コスト削減を図ることができるというすぐれた効果
が得られる。As described above, according to the present invention, a steel having a predetermined composition is rolled, and a steel bar immediately after rolling is directly quenched under predetermined conditions to form a tempered martensite structure having hard carbide on the surface. A steel bar having excellent wear resistance equivalent to that of a hardened material can be obtained online, and an excellent effect that the processing cost of various members of rock crushing machines and construction machines can be reduced can be obtained.
【図１】本発明における圧延−冷却中の棒鋼の温度変化
の一例を示す線図である。FIG. 1 is a diagram showing an example of temperature change of a steel bar during rolling-cooling in the present invention.
【図２】耐摩耗性を求めるために実施したラバ−ホイ−
ル摩耗試験装置の模式図である。[Fig. 2] A rubber wheel carried out to obtain wear resistance.
It is a schematic diagram of a wear test device.
Claims (3)
%、Mn：0.5〜2.0% Sol Al：0.05〜0.1%、N：0.005〜0.0
3%でTi、Zr、Nb、Vのうちの1種または2種以上を0.1〜1.
0%含有し、残部不可避的に混入する元素と鉄よりなる鋼
片を熱間圧延に際して、Ac3〜1050℃の間の温度で仕上
げ圧延を行った後、鋼材表面を強制冷却によりMs点以下
に急冷して後、鋼材内部の保有熱により300〜700℃の間
の温度に自己焼戻しさせて、表層部に焼戻しマルテンサ
イトと硬質炭化物を有する組織を得ることを特徴とする
耐摩耗性棒鋼の製造方法。1. C: O.30 to 1.10% by weight%, Si: 0.1 to 1.8
%, Mn: 0.5 to 2.0% Sol Al: 0.05 to 0.1%, N: 0.005 to 0.0
0.1% to 1% or more of Ti, Zr, Nb, and V at 3%.
At the time of hot rolling a steel slab containing 0% and the balance unavoidably mixed elements and iron, after finish rolling at a temperature between Ac 3 and 1050 ° C, the steel surface is forced to cool down to the Ms point or less. Of the wear-resistant steel bar characterized by obtaining a structure having tempered martensite and hard carbide in the surface layer by self-tempering to a temperature between 300 and 700 ° C by the retained heat inside the steel after quenching to Production method.
%、Mn：0.5〜2.0% Sol Al：0.05〜0.1%、N：0.005〜0.0
3%でTi、Zr、Nb、Vのうちの1種または2種以上を0.1〜1.
0%含有し、さらにNi：O.1〜1.0%、Cr：O.1〜1.5%、Mo：
O.05〜0.5%、B：O.0005〜0.0050%のうちの少なくとも1
種を含有し、残部不可避的に混入する元素と鉄よりなる
鋼片を熱間圧延に際して、Ac3〜1050℃の間の温度で仕
上げ圧延を行った後、鋼材表面を強制冷却によりMs点以
下に急冷して後、鋼材内部の保有熱により300℃〜700℃
の間の温度に自己焼戻しさせて、表層部に焼戻しマルテ
ンサイトと硬質炭化物を有する組織を得ることを特徴と
する耐摩耗性棒鋼の製造方法。2. C: O.30 to 1.10% by weight%, Si: 0.1 to 1.8
%, Mn: 0.5 to 2.0% Sol Al: 0.05 to 0.1%, N: 0.005 to 0.0
0.1% to 1% or more of Ti, Zr, Nb, and V at 3%.
0% content, Ni: O.1-1.0%, Cr: O.1-1.5%, Mo:
O.05 to 0.5%, B: at least 1 of O.0005 to 0.0050%
Containing species, in between the balance inevitably mixed elemental heat the steel piece made of iron rolling, after finishing rolling at a temperature between Ac 3 to 1050 ° C., Ms point or lower by forced cooling steel surface After quenching to 300 ℃ ~ 700 ℃ due to the internal heat of the steel
A method for producing a wear-resistant steel bar, which is characterized in that a structure having tempered martensite and hard carbide in a surface layer portion is obtained by self-tempering at a temperature between the temperatures.
0.03〜0.30%、Se：0.01〜0.10%、Te：0.01〜0.10%、C
a：0.001〜0.010%のうちの1種または2種以上を含有する
請求項１または２のいずれかに記載の耐摩耗性棒鋼の製
造方法。3. S: 0.01 to 0.10%, Pb: 0.03 to 0.30%, Bi:
0.03 to 0.30%, Se: 0.01 to 0.10%, Te: 0.01 to 0.10%, C
a: The method for producing a wear-resistant steel bar according to claim 1 or 2, containing one or more of 0.001 to 0.010%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5100446A JP3030675B2 (en) | 1993-04-02 | 1993-04-02 | Manufacturing method of wear-resistant steel bar |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5100446A JP3030675B2 (en) | 1993-04-02 | 1993-04-02 | Manufacturing method of wear-resistant steel bar |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH06287638A true JPH06287638A (en) | 1994-10-11 |
| JP3030675B2 JP3030675B2 (en) | 2000-04-10 |
Family
ID=14274153
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5100446A Expired - Fee Related JP3030675B2 (en) | 1993-04-02 | 1993-04-02 | Manufacturing method of wear-resistant steel bar |
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