JPH11269599A - High strength non-refining steel - Google Patents

High strength non-refining steel

Info

Publication number
JPH11269599A
JPH11269599A JP7580398A JP7580398A JPH11269599A JP H11269599 A JPH11269599 A JP H11269599A JP 7580398 A JP7580398 A JP 7580398A JP 7580398 A JP7580398 A JP 7580398A JP H11269599 A JPH11269599 A JP H11269599A
Authority
JP
Japan
Prior art keywords
content
ferrite
effect
steel
strength
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
Application number
JP7580398A
Other languages
Japanese (ja)
Other versions
JP3584726B2 (en
Inventor
Takatoshi Arai
貴俊 新井
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Corp
Original Assignee
Sumitomo Metal Industries Ltd
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Filing date
Publication date
Application filed by Sumitomo Metal Industries Ltd filed Critical Sumitomo Metal Industries Ltd
Priority to JP07580398A priority Critical patent/JP3584726B2/en
Publication of JPH11269599A publication Critical patent/JPH11269599A/en
Application granted granted Critical
Publication of JP3584726B2 publication Critical patent/JP3584726B2/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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Abstract

PROBLEM TO BE SOLVED: To produce a non-refining steel having high tensile strength and an excellent endurance ratio and suitable as the stock for parts for machine structures including automotive chassis parts at a low cost. SOLUTION: A ferrite-pearlite type high strength non-refining steel is the one having a compsn. composed of, by weight, 0.20 to 0.40% C, 0.4 to 1.0% Si, 1.0 to 2.0% Mn, 0.05% P, 0.03 to 0.10% S, 0.3 to 0.8% Cr, 0.05 to 0.30% V, 0.006 to 0.10% Zr, 0.005 to 0.025% N, 0.005 to 0.07% Al, 0 to 0.10% Nb, 0 to 0.05% Ti, 0 to 0.30% Pb, 0 to 0.010% Ca, 0 to 0.30% Se, 0 to 0.10% Te, 0 to 0.30% Bi, and satisfying C+(1/10)Si+(1/5)Mn-(5/7)S+(5/22)Cr+1.65V>=0.8%, and contg. the balance Fe with impurities.

Description

【発明の詳細な説明】DETAILED DESCRIPTION OF THE INVENTION

【0001】[0001]

【発明の属する技術分野】本発明は、高強度非調質鋼に
関する。より詳しくは、熱間加工後に焼入れ焼戻しの調
質処理を施さなくとも、高い引張強度と優れた耐久比
(疲労強度/引張強度)を有する、自動車用足廻り部品
を初めとする機械構造用部品の素材として好適なフェラ
イト・パーライト型の高強度非調質鋼に関するものであ
る。
[0001] The present invention relates to a high-strength non-heat treated steel. More specifically, mechanical structural parts such as undercarriage parts for automobiles having high tensile strength and an excellent durability ratio (fatigue strength / tensile strength) without performing quenching and tempering after hot working. The present invention relates to a ferrite / pearlite type high-strength non-heat-treated steel suitable as a material for steel.

【0002】[0002]

【従来の技術】機械構造用部品、なかでも自動車用足廻
り鍛造部品としてのホイールハブ、ナックル、アームな
どは、機械構造用の炭素鋼(S45Cなど)あるいは合
金鋼(SCM440など)を用いて熱間鍛造により成形
した後、機械加工と調質処理を施して所望の形状と性能
を確保していた。
2. Description of the Related Art Wheel hubs, knuckles, arms and the like as machine structural parts, especially forged parts for automobiles, are heated using carbon steel (such as S45C) or alloy steel (such as SCM440) for mechanical structures. After forming by cold forging, machining and refining treatment were performed to secure a desired shape and performance.

【0003】しかし、調質処理には多くのエネルギーと
コストを費やす。更に、中・高C鋼を焼入れすると焼割
れが生じることが多いし、たとえ焼割れを生じなくとも
大きな変態歪が生ずるため「曲がり」が大きくなって、
曲がり取りの矯正工程が必要となる。そこで近年、省エ
ネルギーの社会的要請に応え、且つ一方ではコスト低減
及び製造工程の簡略化を図るために、熱間鍛造のままで
使用できる非調質鋼の開発が盛んに行われてきた。
However, the refining process consumes a lot of energy and cost. Furthermore, quenching often occurs when medium and high C steels are quenched, and even if there is no quenching cracking, a large transformation strain occurs, resulting in a large "bending".
A straightening process for bending is required. Therefore, in recent years, non-heat-treated steels that can be used as they are in hot forging have been actively developed in order to meet the social demands for energy savings and to reduce costs and simplify the manufacturing process.

【0004】非調質鋼としては、ベイナイト型、マルテ
ンサイト型及びフェライト・パーライト型の非調質鋼が
知られている。このうち、ベイナイト型とマルテンサイ
ト型の非調質鋼では高い強度が得られるものの被削性が
低い。このため機械加工による仕上げ成形に難があり、
加えて大きな変態歪が生ずるため「曲がり」が大きくな
るという問題があって、曲がり取りの矯正工程が必要な
ためにコストアップにつながる。例えば、特開平4−1
76842号公報で提案されているベイナイト型の「熱
間鍛造用非調質鋼」においてもなお上記の被削性や曲が
り発生の面で問題が残るものであった。
[0004] As non-heat treated steels, bainite, martensite and ferrite / pearlite non-heat treated steels are known. Of these, bainite-type and martensite-type non-heat treated steels provide high strength but low machinability. For this reason, there is difficulty in finish forming by machining,
In addition, there is a problem that "bending" becomes large due to generation of a large transformation strain, and a step of correcting the bending is required, which leads to an increase in cost. For example, Japanese Patent Application Laid-Open No. 4-1
The bainite type "non-heat treated steel for hot forging" proposed in Japanese Patent No. 76842 still has a problem in terms of the above-described machinability and bending.

【0005】特開平4−210449号公報には、その
組織が主としてフェライト及びベイナイトで一部パーラ
イトが混在した「高靭性熱間鍛造用非調質鋼」が開示さ
れている。この公報で提案された技術は、組織にフェラ
イトとパーライトを含むため、ベイナイト単相の場合に
比べて変態歪による「曲がり」は幾分解消されるもので
ある。しかし、組織中にベイナイトが占める割合が高い
場合には変態歪の発生による「曲がり」を矯正する工程
が必要でコストアップが避けられないものであった。
[0005] Japanese Patent Application Laid-Open No. Hei 4-210449 discloses a "high-toughness non-heat-treated steel for hot forging" whose structure is mainly ferrite and bainite and partially contains pearlite. In the technique proposed in this publication, since the structure contains ferrite and pearlite, "bending" due to transformation strain is somewhat eliminated as compared with the case of bainite single phase. However, when bainite occupies a high proportion in the structure, a step of correcting "bending" due to the occurrence of transformation strain is required, and a cost increase is inevitable.

【0006】一方、フェライト・パーライト型の非調質
鋼に関する技術として、例えば特開昭63−19984
8号公報、特開平7−70698号公報、特開平7−1
02340号公報が開示されている。
On the other hand, as a technique relating to a ferrite / pearlite type non-heat treated steel, for example, Japanese Patent Application Laid-Open No. 63-19998
No. 8, JP-A-7-70698, JP-A 7-1
No. 02340 is disclosed.

【0007】このうち、特開昭63−199848号公
報にはAl含有量を0.020%未満に規制することに
よって、Vの窒化物と固溶Nとによるフェライトの強化
を図った「耐疲労性及び切削性にすぐれる熱間鍛造用非
調質鋼」が開示されている。しかし、この公報で提案さ
れた非調質鋼はAlの含有量を低く抑えたものであるた
め、AlNによる結晶粒微細化効果が得られないことも
あってその耐久比は実施例からも明らかなように高々
0.55である。
Among them, Japanese Patent Application Laid-Open No. 63-199848 discloses an attempt to strengthen ferrite by V nitride and solid solution N by limiting the Al content to less than 0.020%. Non-heat treated steel for hot forging having excellent workability and machinability ”is disclosed. However, since the non-heat treated steel proposed in this publication has a low content of Al, the effect of AlN on the grain refinement may not be obtained. It is at most 0.55.

【0008】特開平7−70698号公報には、特定の
化学組成からなる「高疲労強度快削非調質鋼」が開示さ
れている。しかし、この公報で提案された技術は900
MPa以上の引張強度と0.5以上の耐久比を有する被
削性に優れた非調質鋼を提供することを目的とするもの
であって、前記の非調質鋼は上記目標は満足するもの
の、その実施例の記載からも明らかなように耐久比は高
々0.54である。これは、結晶粒微細化のための配慮
が充分なされていないためである。
[0008] Japanese Patent Application Laid-Open No. 7-70698 discloses "high fatigue strength free-cut non-heat treated steel" having a specific chemical composition. However, the technology proposed in this publication is 900
It is an object of the present invention to provide a non-heat treated steel excellent in machinability having a tensile strength of not less than MPa and a durability ratio of not less than 0.5, and the above non-heat treated steel satisfies the above-mentioned target. However, as is clear from the description of the example, the durability ratio is at most 0.54. This is because sufficient consideration has not been given to crystal grain refinement.

【0009】特開平7−102340号公報には、熱間
鍛造後に冷却した組織の90%以上がフェライト+パー
ライトからなる特定の化学組成を有する鋼材を200〜
700℃で時効処理する「疲労特性に優れる非調質鋼の
製造方法」が開示されている。しかし、この公報で提案
された技術は調質処理の焼入れは省略できるものの焼戻
しと同様な時効のための熱処理を行う必要があるのでエ
ネルギーコストが嵩む。更に、この公報で提案された方
法で製造された「非調質鋼」の耐久比もその実施例にお
ける記載から明らかなように高々0.58である。
Japanese Patent Application Laid-Open No. 7-102340 discloses that a steel material having a specific chemical composition of 90% or more of ferrite + pearlite in which at least 90% of the structure is cooled after hot forging is used.
A method for producing a non-heat treated steel having excellent fatigue properties, which is subjected to aging treatment at 700 ° C., is disclosed. However, the technology proposed in this publication can omit the quenching of the refining treatment, but requires heat treatment for aging similar to tempering, so that the energy cost increases. Further, the durability ratio of the "non-heat treated steel" manufactured by the method proposed in this publication is at most 0.58 as is clear from the description in the examples.

【0010】[0010]

【発明が解決しようとする課題】本発明は、上記現状に
鑑みなされたもので、通常の熱間鍛造と冷却の条件で、
それも鍛造後の時効処理を含めて熱処理を行うことなく
非調質のままで、例えば、800MPa以上の高い引張
強度と、0.60以上の優れた耐久比を有し、自動車用
足廻り部品を初めとする機械構造用部品の素材として好
適なフェライト・パーライト型の高強度非調質鋼を低コ
ストで提供することを目的とする。
DISCLOSURE OF THE INVENTION The present invention has been made in view of the above-mentioned circumstances, and is based on ordinary hot forging and cooling conditions.
It has a high tensile strength of 800 MPa or more and an excellent durability ratio of 0.60 or more, for example, and has no heat treatment including heat treatment including aging treatment after forging. It is an object of the present invention to provide a ferrite-pearlite type high-strength non-heat-treated steel suitable as a material for parts for machine structures including the above at low cost.

【0011】[0011]

【課題を解決するための手段】本発明の要旨は、下記に
示す高強度非調質鋼にある。
The gist of the present invention resides in the following high-strength non-heat treated steel.

【0012】すなわち、「重量%で、C:0.20〜
0.40%、Si:0.4〜1.0%、Mn:1.0〜
2.0%、P:0.05%以下、S:0.03〜0.1
0%、Cr:0.3〜0.8%、V:0.05〜0.3
0%、Zr:0.006〜0.10%、N:0.005
〜0.025%、Al:0.005〜0.07%、N
b:0〜0.10%、Ti:0〜0.05%、Pb:0
〜0.30%、Ca:0〜0.010%、Se:0〜
0.30%、Te:0〜0.10%及びBi:0〜0.
30%を含み、更に、式中の元素記号をその元素の重量
%での含有量として下記式で表されるfn1が0.8
%以上で、残部はFe及び不可避不純物の化学組成から
なるフェライト・パーライト型の高強度非調質鋼。
That is, "in weight%, C: 0.20 to 0.20%
0.40%, Si: 0.4 to 1.0%, Mn: 1.0 to
2.0%, P: 0.05% or less, S: 0.03 to 0.1
0%, Cr: 0.3-0.8%, V: 0.05-0.3
0%, Zr: 0.006 to 0.10%, N: 0.005
0.025%, Al: 0.005 to 0.07%, N
b: 0 to 0.10%, Ti: 0 to 0.05%, Pb: 0
~ 0.30%, Ca: 0 ~ 0.010%, Se: 0 ~
0.30%, Te: 0 to 0.10%, and Bi: 0 to 0.
Fn1 represented by the following formula, where the symbol of the element in the formula is the content in weight% of the element, is 0.8%.
%, With the balance being ferrite-pearlite high-strength non-heat treated steel consisting of the chemical composition of Fe and unavoidable impurities.

【0013】 fn1=C+(1/10)Si+(1/5)Mn−(5/7)S+(5/22 )Cr+1.65V・・・・・」である。Fn1 = C + (1/10) Si + (1/5) Mn− (5/7) S + (5/22) Cr + 1.65V...

【0014】本発明者らは、前記した目的を達成するた
め非調質鋼の化学組成及び組織について種々検討を重ね
た結果、下記の知見を得た。
The present inventors have conducted various studies on the chemical composition and structure of the non-heat treated steel in order to achieve the above object, and have obtained the following findings.

【0015】(a)特定の化学組成を有するフェライト
・パーライト型の非調質鋼の強度は前記した式で整理
でき、式の値が0.8%以上であれば800MPa以
上の引張強度が安定して得られる。
(A) The strength of a ferritic / pearlite type non-heat treated steel having a specific chemical composition can be arranged by the above-mentioned formula. If the value of the formula is 0.8% or more, the tensile strength of 800 MPa or more is stable. Is obtained.

【0016】(b)フェライト・パーライト型の非調質
鋼の耐久比は、組織の微細化、フェライト分率の増大及
びフェライトの強化によって増大させることができる。
(B) The durability ratio of ferrite-pearlite type non-heat treated steel can be increased by refining the structure, increasing the ferrite fraction, and strengthening the ferrite.

【0017】(c)Zrを添加して鋼中に微細なZrの
炭窒化物を析出させておけば、熱間鍛造のための加熱時
にオーステナイト粒が粗大化するのを防止できるし、鍛
造後の冷却時にフェライト析出サイトが増えるので、微
細な組織が得られるとともにフェライト分率が増大す
る。
(C) By adding Zr to precipitate fine Zr carbonitrides in the steel, it is possible to prevent austenite grains from becoming coarse during heating for hot forging, Since the number of ferrite precipitation sites increases during cooling, a fine structure can be obtained and the ferrite fraction increases.

【0018】(d)適正量のMnとSを含有させてMn
Sを生成させれば、このMnSが鍛造後の冷却過程での
フェライト析出サイトとなるので、組織の微細化とフェ
ライト分率の増大が図れる。
(D) containing an appropriate amount of Mn and S
If S is generated, this MnS becomes a ferrite precipitation site in the cooling process after forging, so that the structure can be refined and the ferrite fraction can be increased.

【0019】(e)フェライト分率を増大させるととも
にフェライトを強化するためには、C含有量を低減して
SiとVを含有させれば良い。
(E) In order to increase the ferrite fraction and strengthen the ferrite, the C content should be reduced to include Si and V.

【0020】(f)フェライト・パーライト型の非調質
鋼の耐久比の増大は、鋼材の延性(絞り)を高めること
によっても達成できる。
(F) The increase in the durability ratio of the ferrite-pearlite type non-heat treated steel can also be achieved by increasing the ductility (drawing) of the steel material.

【0021】(g)Crを含有させればパーライトのラ
メラ間隔が小さくなって鋼材の絞りを高めることができ
る。
(G) When Cr is contained, the lamella spacing of pearlite is reduced, and the drawing of steel material can be increased.

【0022】(h)特定の化学組成を有するフェライト
・パーライト型の非調質鋼材から切り出した円形断面の
試験片を用いて引張強試験を行った時、50%以上の絞
りが得られれば0.60以上の耐久比が得られる。
(H) When a tensile strength test is performed using a test piece having a circular cross section cut out of a ferrite / pearlite type non-heat treated steel material having a specific chemical composition, if a drawing of 50% or more is obtained, 0 is obtained. A durability ratio of .60 or more is obtained.

【0023】(i)上記(h)の50%以上の絞りは、
フェライト・パーライト組織においてフェライトがJI
S粒度番号6以上の細粒である場合に安定して得られ
る。
(I) The aperture of 50% or more of (h) is
Ferrite is JI in ferrite-pearlite structure
S can be obtained stably when the fine particles have an S particle number of 6 or more.

【0024】本発明は、上記の知見に基づいて完成され
たものである。
The present invention has been completed based on the above findings.

【0025】[0025]

【発明の実施の形態】以下、本発明の各要件について詳
しく説明する。なお、化学成分の含有量の「%」は「重
量%」を意味する。
DESCRIPTION OF THE PREFERRED EMBODIMENTS Each requirement of the present invention will be described in detail below. In addition, “%” of the content of the chemical component means “% by weight”.

【0026】C:0.20〜0.40% Cは、フェライト・パーライト組織において引張強度で
800MPa以上の高強度を確保するのに有効な元素で
ある。その効果を得るためには0.20%以上の含有量
を必要とする。しかし、0.40%を超えて含有すると
フェライト分率が低下して耐久比が0.60を下回るよ
うになる。したがって、Cの含有量を0.20〜0.4
0%とした。
C: 0.20 to 0.40% C is an element effective for securing a high tensile strength of 800 MPa or more in a ferrite-pearlite structure. To obtain the effect, a content of 0.20% or more is required. However, if the content exceeds 0.40%, the ferrite fraction decreases, and the durability ratio falls below 0.60. Therefore, the content of C is set to 0.20 to 0.4.
0%.

【0027】Si:0.4〜1.0% Siは、脱酸を促進するとともにフェライト中に固溶し
てフェライトを強化して耐久比を高める作用を有する。
前記の効果を充分発揮させるためには、Siの含有量を
0.4%以上とすることが必要である。しかし、Siを
過剰に添加すると前記の効果が飽和するばかりか鍛造の
ための加熱で鋼材表面の脱炭が進んで表面強度が下がっ
てしまう。特に、Si含有量が1.0%を超えると鋼材
表面の脱炭が著しくなる。したがってSiの含有量を
0.4〜1.0%とした。
Si: 0.4-1.0% Si has the effect of promoting deoxidation and also forming a solid solution in ferrite to strengthen ferrite and increase the durability ratio.
In order to sufficiently exhibit the above effects, it is necessary to make the Si content 0.4% or more. However, when Si is excessively added, the above-described effect is not only saturated, but also decarburization of the steel material surface is advanced by heating for forging, and the surface strength is reduced. In particular, if the Si content exceeds 1.0%, the decarburization of the steel material surface becomes remarkable. Therefore, the content of Si is set to 0.4 to 1.0%.

【0028】Mn:1.0〜2.0 Mnは、脱酸作用及び強度を高める作用を有する。更
に、Sと結合したMnSが熱間鍛造後の冷却過程におけ
るフェライトの析出サイトとして働き組織の微細化とフ
ェライト分率の増大に寄与する。こうした効果を確保す
るためにはMnは1.0%以上の含有量を必要とする。
しかし、2.0%を超えて含有させてもその効果は飽和
してコストが嵩む。更に、焼入れ性が高くなりすぎてベ
イナイトや島状マルテンサイトが生成するので被削性が
低下する。このため、Mn含有量を1.0〜2.0%と
した。
Mn: 1.0 to 2.0 Mn has a deoxidizing effect and an effect of increasing strength. Further, MnS combined with S serves as a precipitation site of ferrite in a cooling process after hot forging, and contributes to refinement of the structure and increase in the ferrite fraction. In order to secure such an effect, the content of Mn needs to be 1.0% or more.
However, even if the content exceeds 2.0%, the effect is saturated and the cost increases. Further, the hardenability becomes too high, and bainite and island-like martensite are formed, so that the machinability decreases. For this reason, the Mn content is set to 1.0 to 2.0%.

【0029】P:0.05%以下 Pは鋼中に不純物として含有されるものであり、必須成
分として添加しなくても良い。添加すれば被削性と耐久
比を高める作用を有する。この効果を確実に得るには、
Pは0.010%以上の含有量とすることが好ましい。
しかし、その含有量が0.05%を超えると靭性の著し
い低下を招く。したがって、Pの含有量を0.05%以
下とした。
P: 0.05% or less P is contained as an impurity in steel, and need not be added as an essential component. When added, it has the effect of improving machinability and durability ratio. To ensure this effect,
It is preferable that the content of P is 0.010% or more.
However, when the content exceeds 0.05%, the toughness is significantly reduced. Therefore, the content of P is set to 0.05% or less.

【0030】S:0.03〜0.10% Sは、鋼の被削性を高めるとともに、Mnと結合したM
nSが熱間鍛造後の冷却過程におけるフェライトの析出
サイトとして働き組織の微細化とフェライト分率の増大
に寄与する。しかし、その含有量が0.03%未満では
添加効果に乏しい。一方、0.10%を超えて含有させ
ても前記の効果が飽和するし、靭性の低下を招く。した
がって、S含有量を0.03〜0.10%とした。
S: 0.03 to 0.10% S enhances the machinability of steel and combines M with Mn.
nS acts as a precipitation site of ferrite in the cooling process after hot forging, and contributes to refinement of the structure and increase in the ferrite fraction. However, if the content is less than 0.03%, the effect of addition is poor. On the other hand, if the content exceeds 0.10%, the above effect is saturated and the toughness is reduced. Therefore, the S content is set to 0.03 to 0.10%.

【0031】Cr:0.3〜0.8% Crは、固溶強化元素として強度を高めるとともにパー
ライトラメラ間隔を小さくして延性(絞り)を大きくし
て耐久比を高める作用を有する。しかし、その含有量が
0.3%未満では添加効果に乏しい。一方、0.8%を
超えて含有させてもその効果は飽和してコストが嵩む。
更に、焼入れ性が高くなりすぎてベイナイトや島状マル
テンサイトが生成するので被削性が低下する。このた
め、Cr含有量を0.3〜0.8%とした。
Cr: 0.3-0.8% Cr has the effect of increasing the strength as a solid solution strengthening element, reducing the pearlite lamella spacing, increasing ductility (drawing), and increasing the durability ratio. However, if the content is less than 0.3%, the effect of addition is poor. On the other hand, if the content exceeds 0.8%, the effect is saturated and the cost increases.
Further, the hardenability becomes too high, and bainite and island-like martensite are formed, so that the machinability decreases. For this reason, the Cr content is set to 0.3 to 0.8%.

【0032】V:0.05〜0.30% Vは、析出強化元素であり、フェライトを強化して耐久
比を高める作用を有する。しかし、その含有量が0.0
5%未満では前記の効果が得難い。一方、0.30%を
超えて含有させても前記効果は飽和し、コストのみが上
昇して経済性を損なうことになる。したがって、Vの含
有量を0.05〜0.30%とした。
V: 0.05 to 0.30% V is a precipitation strengthening element and has the effect of strengthening ferrite and increasing the durability ratio. However, the content is 0.0
If it is less than 5%, it is difficult to obtain the above effect. On the other hand, if the content exceeds 0.30%, the effect is saturated, and only the cost is increased, which impairs economic efficiency. Therefore, the content of V is set to 0.05 to 0.30%.

【0033】Zr:0.006〜0.10% Zrは、C及びNと結合してZr炭窒化物として析出
し、オーステナイト結晶粒の粗大化を防止するととも
に、上記Zr炭窒化物が鍛造後の冷却時にフェライトの
析出サイトとなって組織の微細化及びフェライト分率の
増大にも寄与する。しかし、その含有量が0.006%
未満では所望の効果が得られない。一方、Zrを0.1
0%を超えて含有させても前記効果は飽和しコストが嵩
むばかりである。したがって、Zr含有量を0.006
〜0.10%とした。
Zr: 0.006% to 0.10% Zr combines with C and N and precipitates as Zr carbonitride to prevent coarsening of austenite crystal grains and to prevent the above Zr carbonitride from being forged. During cooling, it becomes a ferrite precipitation site and contributes to the refinement of the structure and an increase in the ferrite fraction. However, its content is 0.006%
If it is less than 30, the desired effect cannot be obtained. On the other hand, when Zr is 0.1
Even if the content exceeds 0%, the effect is saturated and the cost is increased. Therefore, when the Zr content is 0.006
0.10.10%.

【0034】N:0.005〜0.025% Nは、CとともにVやZrと結合してV炭窒化物やZr
炭窒化物として析出し強度を高める作用を有する。又、
上記のZr炭窒化物及びAlと結合したAlNがオース
テナイト粒の粗大化を防止するので組織の微細化にも有
効である。しかし、その含有量が0.005%未満では
前記の効果が得難い。一方、0.025%を超えて含有
させてもその効果は飽和するばかりか、熱間加工性の劣
化を招くようになる。したがって、Nの含有量を、0.
005〜0.025%とした。
N: 0.005 to 0.025% N is combined with V and Zr together with C to form V carbonitride or Zr.
It has the effect of precipitating as carbonitride and increasing the strength. or,
The above-mentioned AlN combined with Zr carbonitride and Al prevents the austenite grains from being coarsened, so that it is also effective in refining the structure. However, if the content is less than 0.005%, it is difficult to obtain the above effects. On the other hand, if the content exceeds 0.025%, the effect is not only saturated, but also causes deterioration of hot workability. Therefore, the content of N is set to 0.
005 to 0.025%.

【0035】Al:0.005〜0.07% Alは、脱酸作用を有する。更に、AlはNとともにA
lNを形成してオーステナイト粒の粗大化を防止し、組
織を微細化して耐久比を高める作用を有する。しかし、
その含有量が0.005%未満では添加効果に乏しく、
0.07%を超えると酸化物系の介在物が増加して切削
時に工具寿命の低下を招くとともに、表皮下介在物によ
って疲労特性の低下をきたす。したがって、Alの含有
量を0.005〜0.07%とした。
Al: 0.005 to 0.07% Al has a deoxidizing effect. Further, Al is A together with N
It has the effect of forming 1N to prevent coarsening of austenite grains and to refine the structure to increase the durability ratio. But,
If the content is less than 0.005%, the effect of addition is poor,
When the content exceeds 0.07%, oxide-based inclusions increase to cause a decrease in tool life during cutting, and the subcutaneous subsurface inclusions lower fatigue characteristics. Therefore, the content of Al is set to 0.005 to 0.07%.

【0036】Nb:0〜0.10% Nbは添加しなくても良い。添加すれば窒化物や炭窒化
物を生成して結晶粒を微細化し、強度と耐久比を高める
作用を有する。この効果を確実に得るには、Nbは0.
003%以上の含有量とすることが望ましい。しかし、
0.10%を超えて含有させると鋼の熱間加工性が大き
く低下するようになる。したがって、Nbの含有量を0
〜0.10%とした。
Nb: 0 to 0.10% Nb may not be added. If added, it has the effect of forming nitrides and carbonitrides to refine the crystal grains and increase the strength and durability ratio. In order to ensure this effect, Nb should be set to 0.1.
Desirably, the content is at least 003%. But,
If the content exceeds 0.10%, the hot workability of steel will be greatly reduced. Therefore, the content of Nb is reduced to 0.
0.10.10%.

【0037】Ti:0〜0.05% Tiは添加しなくても良い。添加すれば、オーステナイ
ト結晶粒の粗大化を防止するとともに、組織の微細化及
びフェライト分率の増大にも寄与する。この効果を確実
に得るには、Tiは0.003%以上の含有量とするこ
とが望ましい。しかし、0.05%を超えて含有させて
も前記の効果は飽和しコストが嵩むばかりである。した
がって、Ti含有量を0〜0.05%とした。
Ti: 0 to 0.05% Ti need not be added. The addition prevents the austenite crystal grains from becoming coarse, and contributes to the refinement of the structure and the increase in the ferrite fraction. To ensure this effect, the content of Ti is desirably 0.003% or more. However, even if the content exceeds 0.05%, the above effect is saturated and the cost increases. Therefore, the Ti content was set to 0 to 0.05%.

【0038】Pb:0〜0.30% Pbは添加しなくても良い。添加すれば、被削性を高め
る作用を有する。この効果を確実に得るには、Pbは
0.01%以上の含有量とすることが好ましい。しか
し、その含有量が0.30%を超えると熱間加工性及び
疲労強度の著しい低下を招く。したがって、Pb含有量
を0〜0.30%とした。
Pb: 0 to 0.30% Pb may not be added. If added, it has the effect of enhancing machinability. In order to surely obtain this effect, the content of Pb is preferably set to 0.01% or more. However, if the content exceeds 0.30%, the hot workability and the fatigue strength are significantly reduced. Therefore, the Pb content was set to 0 to 0.30%.

【0039】Ca:0〜0.010% Caは添加しなくても良い。添加すれば、被削性を高め
る作用を有する。この効果を確実に得るには、Caは
0.0005%以上の含有量とすることが好ましい。し
かし、その含有量が0.010%を超えると熱間加工性
及び疲労強度の著しい低下を招く。したがって、Ca含
有量を0〜0.010%とした。
Ca: 0 to 0.010% Ca may not be added. If added, it has the effect of enhancing machinability. In order to surely obtain this effect, the content of Ca is preferably set to 0.0005% or more. However, when the content exceeds 0.010%, the hot workability and the fatigue strength are significantly reduced. Therefore, the Ca content was set to 0 to 0.010%.

【0040】Se:0〜0.30% Seは添加しなくても良い。添加すれば、被削性を高め
る作用を有する。この効果を確実に得るには、Seは
0.01%以上の含有量とすることが好ましい。しか
し、その含有量が0.30%を超えると熱間加工性及び
疲労強度の著しい低下を招く。したがって、Seの含有
量を0〜0.30%とした。
Se: 0 to 0.30% Se need not be added. If added, it has the effect of enhancing machinability. In order to surely obtain this effect, the content of Se is preferably set to 0.01% or more. However, if the content exceeds 0.30%, the hot workability and the fatigue strength are significantly reduced. Therefore, the content of Se is set to 0 to 0.30%.

【0041】Te:0〜0.10% Teは添加しなくても良い。添加すれば、被削性を高め
る作用を有する。この効果を確実に得るには、Teは
0.001%以上の含有量とすることが好ましい。しか
し、その含有量が0.10%を超えると熱間加工性及び
疲労強度の著しい低下を招く。したがって、Teの含有
量を0〜0.10%とした。
Te: 0 to 0.10% Te need not be added. If added, it has the effect of enhancing machinability. To ensure this effect, the content of Te is preferably set to 0.001% or more. However, if the content exceeds 0.10%, the hot workability and the fatigue strength are significantly reduced. Therefore, the content of Te is set to 0 to 0.10%.

【0042】Bi:0〜0.30% Biも添加しなくても良い。添加すれば、被削性を高め
る作用を有する。この効果を確実に得るには、Biは
0.001%以上の含有量とすることが好ましい。しか
し、その含有量が0.30%を超えると熱間加工性及び
疲労強度の著しい低下を招く。したがって、Biの含有
量を0〜0.30%とした。
Bi: 0 to 0.30% Bi may not be added. If added, it has the effect of enhancing machinability. To ensure this effect, the content of Bi is preferably set to 0.001% or more. However, if the content exceeds 0.30%, the hot workability and the fatigue strength are significantly reduced. Therefore, the content of Bi is set to 0 to 0.30%.

【0043】fn1:0.8%以上 特定の化学成分を有するフェライト・パーライト型の非
調質鋼の強度は前記式で示されるfn1で整理でき、
この値が0.8%以上であれば引張強度で800MPa
以上の高強度が安定して得られる。したがって、fn1
の値を0.8%以上に規定した。なお、被削性は引張強
度が高くなれば低下し、フェライト・パーライト組織の
場合には、特に引張強度が1100MPaを超えると被
削性の低下が著しくなる。上記fn1の値を1.2%以
下とすれば、引張強度を1100MPa以下に抑えるこ
とが容易になる。したがって、fn1の値は1.2%以
下にすることが好ましい。
Fn1: 0.8% or more The strength of a ferrite / pearlite type non-heat treated steel having a specific chemical composition can be summarized by fn1 represented by the above equation.
If this value is 0.8% or more, the tensile strength is 800 MPa.
The above high strength is stably obtained. Therefore, fn1
Was specified to be 0.8% or more. The machinability decreases as the tensile strength increases, and in the case of a ferrite-pearlite structure, the machinability decreases significantly when the tensile strength exceeds 1100 MPa. If the value of fn1 is 1.2% or less, it becomes easy to suppress the tensile strength to 1100 MPa or less. Therefore, the value of fn1 is preferably set to 1.2% or less.

【0044】上記の化学組成を有する鋼は通常の方法で
溶製された後、例えば通常の方法による熱間での鍛造加
工を受けて(あるいは通常の方法による熱間での圧延や
鍛造を受けた後に更に通常の方法による熱間での鍛造加
工を受けて)所定の形状に成形され、更に必要に応じて
機械加工されてホイールハブ、ナックル、アームなど所
定形状の部品に仕上げられる。なお、所定形状への成形
のための通常の方法による熱間鍛造を行った後の冷却
は、フェライト・パーライト組織となるような冷却速度
での冷却、例えば空冷や放冷とすれば良い。なお、上記
の「通常の熱間鍛造方法」とは900〜1300℃に加
熱してから鍛造する方法をいう。
After the steel having the above chemical composition is melted by a normal method, it is subjected to, for example, hot forging by a normal method (or hot rolling or forging by a normal method). After that, it is further formed into a predetermined shape (by subjecting it to hot forging by a usual method), and is further machined as necessary to be finished into a predetermined shape part such as a wheel hub, a knuckle, an arm or the like. The cooling after the hot forging by a usual method for forming into a predetermined shape may be performed at a cooling rate such as a ferrite-pearlite structure, for example, air cooling or cooling. The “ordinary hot forging method” described above refers to a method of heating to 900 to 1300 ° C. and then forging.

【0045】本発明の非調質鋼を用いれば、前記の通常
の方法による熱間鍛造及びその後のフェライト・パーラ
イト組織となるような冷却速度での冷却によって、フェ
ライトがJIS粒度番号6以上の細粒組織が得られるの
で、後述の実施例に示すように高い引張強度と良好な耐
久比とを確保することができる。
When the non-heat-treated steel of the present invention is used, the ferrite is finely divided into JIS grain size of 6 or more by hot forging according to the above-mentioned ordinary method and subsequent cooling at a cooling rate to obtain a ferrite-pearlite structure. Since a grain structure is obtained, a high tensile strength and a good durability ratio can be secured as shown in Examples described later.

【0046】[0046]

【実施例】表1、表2に示す化学組成の鋼を150kg
真空溶解炉を用い通常の方法によって溶製した。表1に
おける鋼1〜15は化学組成が本発明で規定する範囲内
にある本発明例の鋼であり、表2における鋼16〜31
はその化学組成のいずれかが本発明で規定する含有量の
範囲から外れた比較例の鋼である。
EXAMPLE 150 kg of steel having the chemical composition shown in Tables 1 and 2 was used.
It was melted by a usual method using a vacuum melting furnace. Steels 1 to 15 in Table 1 are steels of Examples of the present invention whose chemical compositions are within the range specified in the present invention, and Steels 16 to 31 in Table 2
Is a steel of a comparative example whose one of the chemical compositions is out of the range of the content specified in the present invention.

【0047】[0047]

【表1】 [Table 1]

【0048】[0048]

【表2】 [Table 2]

【0049】これらの鋼を通常の方法によって鋼片とし
た後、1200〜1250℃に加熱してから、1000
℃の仕上げ温度で直径50mmの丸棒に熱間鍛造した。
次いで、上記の直径50mmに熱間鍛造した丸棒を長さ
100mmに切断し、更に、高周波加熱装置で1200
℃に加熱してから、熱間鍛造プレスを用いて直径が30
mmの丸棒に成形した。熱間鍛造した直径30mmの丸
棒は常温(室温)まで空冷した。
These steels were made into billets by a usual method, and then heated to 1200 to 1250 ° C.
It was hot forged into a round bar having a diameter of 50 mm at a finishing temperature of ° C.
Then, the round bar hot forged to a diameter of 50 mm was cut to a length of 100 mm, and further cut to 1200 mm by a high frequency heating device.
° C, and the diameter is 30 using a hot forging press.
It was formed into a round bar of mm. The hot forged round bar having a diameter of 30 mm was air-cooled to room temperature (room temperature).

【0050】こうして得られた丸棒の中心部から平行部
径が8mmの小野式回転曲げ疲労試験片を切り出して常
温(室温)、大気中、3000rpmの条件で疲労試験
を行ない疲労強度としての疲労限(σw)を求めた。
又、丸棒の中心部からJIS4号引張試験片を切り出
し、常温で引張試験を行って降伏強度(YS)、引張強
度(TS)、伸び及び絞りを測定した。又、直径30m
mで厚さが20mmの試験片を切り出して、光学顕微鏡
による中心部の組織観察を行った。
An Ono-type rotary bending fatigue test piece having a parallel part diameter of 8 mm was cut out from the center of the thus obtained round bar and subjected to a fatigue test at room temperature (room temperature) and in the atmosphere at 3000 rpm to obtain a fatigue strength. Limit (σw) was determined.
Further, a JIS No. 4 tensile test piece was cut out from the center of the round bar, and a tensile test was performed at room temperature to measure the yield strength (YS), tensile strength (TS), elongation, and drawing. In addition, diameter 30m
A test piece having a thickness of 20 m and a thickness of 20 mm was cut out, and the structure at the center was observed with an optical microscope.

【0051】試験結果を表3に示す。Table 3 shows the test results.

【0052】[0052]

【表3】 [Table 3]

【0053】本発明例の鋼である鋼1〜15については
いずれもフェライト・パーライト組織で且つフェライト
がJIS粒度番号6以上の細粒であるため、引張強度で
800MPa以上の高強度と0.60以上の耐久比が得
られている。
Steels 1 to 15 of the present invention all have a ferrite-pearlite structure and the ferrite is fine grains having a JIS particle size number of 6 or more. The above durability ratio is obtained.

【0054】これに対して、成分のいずれかが本発明で
規定する含有量の範囲から外れた比較例の鋼は、少なく
とも引張強度が800MPaに達していないか、耐久比
が0.60に達していない。
On the other hand, the steel of the comparative example in which one of the components is out of the range of the content specified in the present invention has at least a tensile strength not reaching 800 MPa or a durability ratio reaching 0.60. Not.

【0055】なお、本発明例の鋼の前記直径30mmの
丸棒を試験片として、JIS高速度工具鋼SKH51の
φ6mmドリルを使用し、水溶性の潤滑剤を用いて、送
り0.15mm/rev、回転数980rpmの条件で
ドリル穿孔試験を行った。その結果、引張強度が110
0MPa以下であったので被削性に問題がないことを確
認した。
A 30 mm diameter round bar of the steel of the present invention was used as a test piece, a JIS high speed tool steel SKH51 φ6 mm drill was used, and a water-soluble lubricant was used to feed 0.15 mm / rev. The drilling test was performed under the conditions of a rotation speed of 980 rpm. As a result, a tensile strength of 110
Since it was 0 MPa or less, it was confirmed that there was no problem in machinability.

【0056】[0056]

【発明の効果】本発明のフェライト・パーライト型の高
強度非調質鋼を用いれば、引張強度で800MPa以上
の高強度と0.60以上の耐久比とが安定して得られる
ので、機械構造用部品の素材、なかでも自動車用足廻り
鍛造部品としてのホイールハブ、ナックル、アームなど
の素材として利用することができる。
The use of the ferritic / pearlite type high-strength non-heat treated steel of the present invention stably provides a high tensile strength of 800 MPa or more and a durability ratio of 0.60 or more. It can be used as a material for parts for automobiles, especially as a material for wheel hubs, knuckles and arms as forged parts for automobiles.

Claims (1)

【特許請求の範囲】[Claims] 【請求項1】重量%で、C:0.20〜0.40%、S
i:0.4〜1.0%、Mn:1.0〜2.0%、P:
0.05%以下、S:0.03〜0.10%、Cr:
0.3〜0.8%、V:0.05〜0.30%、Zr:
0.006〜0.10%、N:0.005〜0.025
%、Al:0.005〜0.07%、Nb:0〜0.1
0%、Ti:0〜0.05%、Pb:0〜0.30%、
Ca:0〜0.010%、Se:0〜0.30%、T
e:0〜0.10%及びBi:0〜0.30%を含み、
更に、下記式で表されるfn1が0.8%以上で、残
部はFe及び不可避不純物の化学組成からなるフェライ
ト・パーライト型の高強度非調質鋼。 fn1=C+(1/10)Si+(1/5)Mn−(5/7)S+(5/22 )Cr+1.65V・・・・・ 但し、式中の元素記号はその元素の重量%での含有量
を表す。
C. 0.20 to 0.40% by weight, S
i: 0.4 to 1.0%, Mn: 1.0 to 2.0%, P:
0.05% or less, S: 0.03 to 0.10%, Cr:
0.3-0.8%, V: 0.05-0.30%, Zr:
0.006 to 0.10%, N: 0.005 to 0.025
%, Al: 0.005 to 0.07%, Nb: 0 to 0.1
0%, Ti: 0 to 0.05%, Pb: 0 to 0.30%,
Ca: 0 to 0.010%, Se: 0 to 0.30%, T
e: 0 to 0.10% and Bi: 0 to 0.30%,
Furthermore, a ferrite / pearlite type high-strength non-heat treated steel comprising fn1 represented by the following formula of 0.8% or more and the balance being a chemical composition of Fe and unavoidable impurities. fn1 = C + (1/10) Si + (1/5) Mn- (5/7) S + (5/22) Cr + 1.65V where the symbol of the element in the formula is the weight% of the element. Indicates the content.
JP07580398A 1998-03-24 1998-03-24 High strength non-heat treated steel Expired - Lifetime JP3584726B2 (en)

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2004137542A (en) * 2002-10-17 2004-05-13 Sumitomo Metal Ind Ltd Method for manufacturing hot-forged member of microalloyed steel
JP2015025162A (en) * 2013-07-25 2015-02-05 大同特殊鋼株式会社 Ferrite pearlite type non-heat treated steel

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2004137542A (en) * 2002-10-17 2004-05-13 Sumitomo Metal Ind Ltd Method for manufacturing hot-forged member of microalloyed steel
JP2015025162A (en) * 2013-07-25 2015-02-05 大同特殊鋼株式会社 Ferrite pearlite type non-heat treated steel

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