JP5151227B2 - High strength steel plate and manufacturing method thereof - Google Patents
High strength steel plate and manufacturing method thereof Download PDFInfo
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- JP5151227B2 JP5151227B2 JP2007107764A JP2007107764A JP5151227B2 JP 5151227 B2 JP5151227 B2 JP 5151227B2 JP 2007107764 A JP2007107764 A JP 2007107764A JP 2007107764 A JP2007107764 A JP 2007107764A JP 5151227 B2 JP5151227 B2 JP 5151227B2
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- 229910000831 Steel Inorganic materials 0.000 title claims description 83
- 239000010959 steel Substances 0.000 title claims description 83
- 238000004519 manufacturing process Methods 0.000 title claims description 7
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- 238000004804 winding Methods 0.000 claims description 9
- 229910052710 silicon Inorganic materials 0.000 claims description 8
- 229910052758 niobium Inorganic materials 0.000 claims description 7
- 229910052802 copper Inorganic materials 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 6
- 229910052759 nickel Inorganic materials 0.000 claims description 6
- 229910052757 nitrogen Inorganic materials 0.000 claims description 6
- 229910052799 carbon Inorganic materials 0.000 claims description 5
- 238000005097 cold rolling Methods 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 230000000694 effects Effects 0.000 description 15
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- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 3
- 230000032683 aging Effects 0.000 description 3
- 229910052796 boron Inorganic materials 0.000 description 3
- 238000009749 continuous casting Methods 0.000 description 3
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- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 229910001335 Galvanized steel Inorganic materials 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
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- 229910001566 austenite Inorganic materials 0.000 description 2
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- 150000001247 metal acetylides Chemical class 0.000 description 2
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- 230000003746 surface roughness Effects 0.000 description 2
- 241000219307 Atriplex rosea Species 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
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Description
この発明は、自動車用鋼板などに有用な、深絞り性に優れる引張強度TSが340MPa以上の高強度鋼板およびその製造方法に関する。 TECHNICAL FIELD The present invention relates to a high-strength steel sheet having a tensile strength TS excellent in deep drawability, which is useful for automobile steel sheets and the like and having a tensile strength TS of 340 MPa or more, and a method for producing the same.
近年、地球環境保全の観点から、CO2の排出量を規制するため、自動車の燃費改善が要求されている。加えて、衝突時に乗員の安全を確保するため、自動車車体の衝突特性を中心とした安全性向上も要求されている。このため、自動車車体の軽量化および強化が積極的に進められている。 In recent years, in order to regulate CO 2 emissions from the viewpoint of global environmental conservation, improvement in fuel efficiency of automobiles has been demanded. In addition, in order to ensure the safety of passengers in the event of a collision, safety improvements centering on the collision characteristics of automobile bodies are also required. For this reason, the weight reduction and reinforcement of the automobile body are being actively promoted.
自動車車体の軽量化と強化を同時に満たすには、剛性が問題にならない範囲で部品素材を高強度化し、その板厚を薄くすることが効果的であると言われており、最近では高強度鋼板が自動車部品に積極的に使用されている。特に、軽量化効果は、使用する鋼板が高強度であるほど大きくなるため、自動車業界では、例えば、内・外板パネル用材料として引張強度TSが340MPa以上の鋼板が使用される動向にある。また、鋼板を素材とする自動車部品の多くはプレス成形によって製造されるため、深絞り性の指標である平均r値(以下、単にr値と呼ぶ)が1.5以上の高強度鋼板が要求されている。 In order to satisfy the weight reduction and strengthening of automobile bodies at the same time, it is said that it is effective to increase the strength of component materials and reduce the plate thickness within a range where rigidity is not a problem. Are actively used in automotive parts. In particular, since the weight reduction effect increases as the strength of the steel sheet used increases, in the automobile industry, for example, a steel sheet having a tensile strength TS of 340 MPa or more is used as an inner / outer panel material. Also, since many automotive parts made of steel sheets are manufactured by press molding, high strength steel sheets with an average r value (hereinafter simply referred to as r value), which is an index of deep drawability, of 1.5 or more are required. Yes.
高r値を有しながら高強度化する手段としては、極低炭素鋼にTiやNbを添加して固溶炭素や固溶窒素を固着したIF(Interstitial Free)鋼をベースとして、これにSi、Mn、Pなどの固溶強化元素を添加する手法がある。例えば、特許文献1には、C:0.002〜0.015%、Si:1.2%以下、Mn:0.04〜0.8%、P:0.03〜0.10%を含有し、NbをC×3〜(C×8+0.020)%(ここで、Cは元素Cの含有量を表す)となるように添加し、TSが340〜460MPa、r値が1.7以上、伸びElが36%以上で、しかも非時効性である成形性に優れた高張力冷延鋼板が開示されている。しかし、特許文献1に記載の高張力冷延鋼板では、必ずしも優れた耐二次加工脆性が得られないという問題がある。
本発明は、r値が1.5以上と深絞り性に優れ、かつ耐二次加工脆性にも優れるTSが340MPa以上の高強度鋼板およびその製造方法を提供することを目的とする。 An object of the present invention is to provide a high-strength steel sheet having a TS value of 340 MPa or more, which is excellent in deep drawability with an r value of 1.5 or more, and excellent in secondary work brittleness resistance, and a method for producing the same.
本発明者らは、上記のような課題を解決すべく鋭意検討を進めたところ、P、Si、Mn、B量と焼鈍後の高傾角粒界の存在比率を制御することにより、粒界へのPの偏析を抑制でき、高r値で耐二次加工脆性に優れる高強度鋼板が得られることを見出した。 As a result of diligent studies to solve the above problems, the present inventors have controlled the amount of P, Si, Mn, and B and the existence ratio of the high-angle grain boundaries after annealing to the grain boundaries. It was found that segregation of P can be suppressed, and a high-strength steel sheet having a high r value and excellent secondary work brittleness resistance can be obtained.
本発明は、このような知見に基づきなされたもので、質量%で、C:0.0005〜0.04%、Si:0.01〜1.0%、Mn:0.2〜3%、P:0.003〜0.15%、S:0.015%以下、Al:0.005〜0.5%、N:0.006%以下、B:0.0003〜0.01%、およびNb:0.003〜0.1%とTi:0.003〜0.1%のうちから選ばれた少なくとも1種、を含有し、残部がFeおよび不可避的不純物からなる組成を有し、平均r値が1.5以上であり、かつ下記の式(1)で定義されるYが30未満であることを特徴とする高強度鋼板を提供する。
Y=1500XP-3[B]-1.3X・・・(1)
ただし、XP=[P](1+0.1[Si]+0.2[Mn])で、Xは粒界を挟む2つの結晶方位差が15°以上の高傾角粒界のうち結晶方位差が50°以上の高傾角粒界の存在比率(%)を表し、[M]は元素Mの含有量(質量%、ただし[B]はppm)を表す。
The present invention has been made based on such findings, and in mass%, C: 0.0005 to 0.04%, Si: 0.01 to 1.0%, Mn: 0.2 to 3%, P: 0.003 to 0.15%, S: 0.015 %: Less than, Al: 0.005-0.5%, N: 0.006% or less, B: 0.0003-0.01%, and Nb: at least one selected from 0.003-0.1% and Ti: 0.003-0.1% A high-strength steel sheet characterized in that the balance has a composition consisting of Fe and inevitable impurities, the average r value is 1.5 or more, and Y defined by the following formula (1) is less than 30 provide.
Y = 1500XP-3 [B] -1.3X ... (1)
However, XP = [P] (1 + 0.1 [Si] +0.2 [Mn]), and X is a crystallographic difference of 50 ° in the high-angle grain boundary where the crystal orientation difference between two grain boundaries is 15 ° or more. The abundance ratio (%) of the above high-angle grain boundaries is represented, and [M] represents the content of element M (mass%, [B] is ppm).
本発明の高強度鋼板では、上記組成に加えて、さらに、質量%で、Mo:0.05〜0.5%、Cu:0.05〜0.5%およびNi:0.05〜0.5%のうちから選ばれた少なくとも1種を含有させることが好ましい。 In the high-strength steel sheet of the present invention, in addition to the above composition, at least one selected from Mo: 0.05 to 0.5%, Cu: 0.05 to 0.5%, and Ni: 0.05 to 0.5% in addition to the above composition. It is preferable to contain.
本発明の高強度鋼板は、質量%で、C:0.0005〜0.04%、Si:0.01〜1.0%、Mn:0.2〜3%、P:0.003〜0.15%、S:0.015%以下、Al:0.005〜0.5%、N:0.006%以下、B:0.0003〜0.01%、およびNb:0.003〜0.1%とTi:0.003〜0.1%のうちから選ばれた少なくとも1種、を含有し、残部がFeおよび不可避的不純物からなる組成の鋼スラブを、1000〜1300℃に加熱後、800〜950℃の仕上温度で熱間圧延し、熱間圧延後0.5s以内に30℃/s以上の平均冷却速度で鋼板表面温度が400℃以下になるまで冷却した後巻取り、巻取り後の鋼板表面温度が550〜720℃であるように昇温し、次いで50%以上の圧延率で冷間圧延し、400〜700℃の温度範囲を15℃/s以下の平均加熱速度で加熱し、820〜950℃の焼鈍温度で焼鈍することを特徴とする方法により製造できる。 The high-strength steel sheet of the present invention is in mass%, C: 0.0005 to 0.04%, Si: 0.01 to 1.0%, Mn: 0.2 to 3%, P: 0.003 to 0.15%, S: 0.015% or less, Al: 0.005 to 0.5%, N: 0.006% or less, B: 0.0003 to 0.01%, and Nb: 0.003 to 0.1% and Ti: at least one selected from 0.003 to 0.1%, the balance being Fe and inevitable Steel slabs composed of impurities are heated to 1000-1300 ° C, hot-rolled at a finishing temperature of 800-950 ° C, and the steel sheet surface at an average cooling rate of 30 ° C / s or more within 0.5 s after hot rolling Winding after cooling until the temperature reaches 400 ° C or lower, raising the temperature so that the steel sheet surface temperature after winding is 550 to 720 ° C, then cold rolling at a rolling rate of 50% or more, 400 to 700 It can be manufactured by a method characterized by heating at a temperature range of ° C. at an average heating rate of 15 ° C./s or less and annealing at an annealing temperature of 820 to 950 ° C.
本発明の方法では、上記組成に加えて、さらに、質量%で、Mo:0.05〜0.5%、Cu:0.05〜0.5%およびNi:0.05〜0.5%のうちから選ばれた少なくとも1種を含有させることが好ましい。 In the method of the present invention, in addition to the above composition, at least one selected from Mo: 0.05 to 0.5%, Cu: 0.05 to 0.5%, and Ni: 0.05 to 0.5% is further contained in mass%. It is preferable.
本発明により、r値が1.5以上で深絞り性に優れ、かつ耐二次加工脆性にも優れるTSが340MPa以上の高強度鋼板を安定して製造できるようになった。本発明の高強度鋼板を自動車部品に適用することにより、これまでプレス成形が困難であった部品も高強度化が可能となり、自動車車体の衝突安全性や軽量化に十分寄与できるようになった。また、本発明の高強度鋼板は、自動車部品に限らず家電部品やパイプ素材としても適用可能である。 The present invention makes it possible to stably produce a high-strength steel sheet having a TS of 340 MPa or more, which has an r value of 1.5 or more, excellent deep drawability and excellent secondary work brittleness resistance. By applying the high-strength steel sheet of the present invention to automobile parts, it has become possible to increase the strength of parts that have been difficult to press-form so far, and can sufficiently contribute to collision safety and weight reduction of automobile bodies. . Moreover, the high-strength steel sheet of the present invention is applicable not only to automobile parts but also to home appliance parts and pipe materials.
以下に、本発明の詳細を説明する。なお、以下の「%」は、特に断らない限り「質量%」を表す。 Details of the present invention will be described below. The “%” below represents “% by mass” unless otherwise specified.
1)成分
C:0.0005〜0.04%
Cは、高強度化に有効であり、340MPa以上のTSを得るにはC量は0.0005%以上とする。C量が0.04%を超えると深絞り性が低下するので、C量の上限は0.04%、好ましくは0.03%とする。
1) ingredients
C: 0.0005-0.04%
C is effective for increasing the strength. To obtain a TS of 340 MPa or more, the C content is 0.0005% or more. If the C content exceeds 0.04%, the deep drawability deteriorates, so the upper limit of the C content is 0.04%, preferably 0.03%.
Si:0.01〜1.0%
Siは、固溶強化の効果のほか、フェライト変態を促進させ未変態オーステナイト相中のC含有量を上昇させてフェライト相とマルテンサイト相の複合組織を形成させやすくする効果を有する。上記効果を得るには、Si量は0.01%以上、好ましくは0.05%以上とする。一方、Si量が1.0%を超えると熱間圧延時に赤スケールと呼ばれる表面欠陥が発生し、鋼板の表面外観を悪くし、また、溶融亜鉛めっきを施す場合には、めっきの濡れ性を悪くしてめっきむらの発生を招く。したがって、Si量は1.0%以下、好ましくは0.7%以下とする。
Si: 0.01-1.0%
In addition to the effect of solid solution strengthening, Si has the effect of facilitating the ferrite transformation and increasing the C content in the untransformed austenite phase to easily form a composite structure of the ferrite phase and the martensite phase. In order to obtain the above effect, the Si content is 0.01% or more, preferably 0.05% or more. On the other hand, if the Si content exceeds 1.0%, a surface defect called red scale occurs during hot rolling, which deteriorates the surface appearance of the steel sheet. Cause uneven plating. Therefore, the Si content is 1.0% or less, preferably 0.7% or less.
Mn:0.2〜3%
Mnは、熱延鋼板の組織の微細化を介して高r値化に寄与するとともに、固溶強化および細粒化強化により高強度化にも有効である。また、Mnは、Sによる熱間割れを防止するのに有効な元素である。このような観点から、Mn量は0.2%以上とする。440MPa以上のTSを得るには、Mn量は1.2%以上にすることが好ましい。一方、Mn量が3%を超えるとr値や溶接性を劣化させたり、Pとの共存で耐二次加工脆性を低下させるので、Mn量の上限は3%とする。
Mn: 0.2-3%
Mn contributes to increasing the r value through refinement of the structure of the hot-rolled steel sheet, and is also effective for increasing the strength by strengthening solid solution and refining. Mn is an element effective for preventing hot cracking due to S. From such a viewpoint, the Mn content is 0.2% or more. In order to obtain TS of 440 MPa or more, the Mn content is preferably 1.2% or more. On the other hand, if the Mn amount exceeds 3%, the r value and weldability are deteriorated, and the secondary work brittleness resistance is lowered by coexistence with P. Therefore, the upper limit of the Mn amount is 3%.
P:0.003〜0.15%
Pは、固溶強化の効果を有する。しかし、P量が0.003%未満では、その効果が現れないだけでなく、製鋼時の脱りんコストの上昇を招く。したがって、P量は0.003%以上、好ましくは0.01%以上とする。一方、P量が0.15%を超えると、Pが粒界に偏析して耐2次加工脆性および溶接性を劣化させる。また、溶融亜鉛めっき後の合金化処理時に、Pはめっき層と鋼板の界面におけるFeの拡散を抑制して合金化処理性を劣化させるので、高温での合金化処理が必要となり、パウダリングやチッピングなどのめっき剥離が生じやすくなる。したがって、P量の上限は0.15%とする。
P: 0.003-0.15%
P has a solid solution strengthening effect. However, if the amount of P is less than 0.003%, not only the effect does not appear, but also the dephosphorization cost at the time of steelmaking increases. Therefore, the P content is 0.003% or more, preferably 0.01% or more. On the other hand, if the amount of P exceeds 0.15%, P segregates at the grain boundaries and deteriorates secondary work embrittlement resistance and weldability. In addition, during alloying after hot dip galvanizing, P suppresses the diffusion of Fe at the interface between the plating layer and the steel sheet and degrades the alloying processability. Therefore, alloying at high temperatures is required, and powdering and Plating peeling such as chipping is likely to occur. Therefore, the upper limit of the P content is 0.15%.
S:0.015%以下
Sは、熱間割れの原因になるほか、鋼中で介在物として存在して鋼板の諸特性を劣化させる。したがって、S量は0.015%以下にする必要があるが、できるだけ低減することが好ましい。
S: 0.015% or less
In addition to causing hot cracking, S is present as an inclusion in steel and deteriorates various properties of the steel sheet. Therefore, the S amount needs to be 0.015% or less, but is preferably reduced as much as possible.
Al:0.005〜0.5%
Alは、鋼の脱酸元素として有用であるほか、固溶NをAlNとして析出させ耐常温時効性を向上させる作用がある。そのため、Al量は0.005%以上とする。一方、Al量が0.5%を超えると合金コスト増や表面欠陥の誘発を招くので、Al量は0.5%以下とする。
Al: 0.005-0.5%
In addition to being useful as a deoxidizing element for steel, Al has the effect of improving the normal temperature aging resistance by precipitating solute N as AlN. Therefore, the Al content is 0.005% or more. On the other hand, if the Al content exceeds 0.5%, alloy costs increase and surface defects are induced, so the Al content is 0.5% or less.
N:0.006%以下
Nが多量に存在すると耐常温時効性を劣化させるため、その分多量のAlやTiの添加が必要となる。したがって、N量の上限は0.006%にする必要があるが、できるだけ低減することが好ましい。
N: 0.006% or less
When N is present in a large amount, the room temperature aging resistance is deteriorated, so that a large amount of Al or Ti needs to be added accordingly. Therefore, the upper limit of the N amount needs to be 0.006%, but is preferably reduced as much as possible.
B:0.0003〜0.01%
Bは、粒界を強化し、耐二次加工脆性を向上させるのに有効な元素である。そのため、B量は0.0003%以上とする。しかし、B量が0.01%を超えるとその効果は飽和するため、B量は0.01%以下とする。
B: 0.0003-0.01%
B is an element effective for strengthening grain boundaries and improving secondary work brittleness resistance. Therefore, the B amount is 0.0003% or more. However, since the effect is saturated when the amount of B exceeds 0.01%, the amount of B is set to 0.01% or less.
Nb:0.003〜0.1%とTi:0.003〜0.1%のうちから選ばれた少なくとも1種
Nbは、熱延鋼板の組織を微細化したり、熱延鋼板中にNbCとして析出して固溶C量を減少させて高r値化に寄与する。このような観点から、Nb量は0.003%以上にする必要がある。一方、過剰のNb添加は延性を低下させることになるので、Nb量の上限は0.1%とする。
Nb: at least one selected from 0.003-0.1% and Ti: 0.003-0.1%
Nb refines the structure of the hot-rolled steel sheet or precipitates as NbC in the hot-rolled steel sheet, thereby reducing the amount of dissolved C and contributing to a high r value. From such a viewpoint, the Nb amount needs to be 0.003% or more. On the other hand, excessive Nb addition reduces ductility, so the upper limit of Nb content is 0.1%.
Tiも、Nbと同様、熱延鋼板の組織を微細化させ、また熱延鋼板中に炭化物として析出して固溶C量を減少させて高r値化に寄与する。ただし、熱延鋼板の微細化の効果はNbの方が大きいので、Nb添加鋼に対して、適宜Tiを添加するのが好ましい。さらに、Tiは熱間圧延の高温域でS、Nと析出物を形成することで、高r値化など、成形性の向上に寄与する。このような観点から、Ti量は0.003%以上にする必要がある。一方、過剰のTi添加は、Nbと同様、延性を低下させることになるので、Ti量の上限は0.1%とする。 Ti, like Nb, refines the structure of the hot-rolled steel sheet and also precipitates as carbides in the hot-rolled steel sheet, thereby reducing the amount of dissolved C and contributing to a higher r value. However, since the effect of refinement of the hot-rolled steel sheet is larger in Nb, it is preferable to add Ti appropriately to the Nb-added steel. Furthermore, Ti contributes to the improvement of formability such as high r value by forming precipitates with S and N in the high temperature range of hot rolling. From such a viewpoint, the Ti amount needs to be 0.003% or more. On the other hand, excessive addition of Ti reduces ductility as with Nb, so the upper limit of Ti content is 0.1%.
残部はFeおよび不可避的不純物である。ここで、不可避的不純物としては、0.01%以下のSb、0.1%以下のSn、0.01%以下のZn、0.1%以下のCoなどが挙げられる。 The balance is Fe and inevitable impurities. Here, unavoidable impurities include 0.01% or less Sb, 0.1% or less Sn, 0.01% or less Zn, 0.1% or less Co, and the like.
また、上記成分組成に加え、Mo:0.05〜0.5%、Cu:0.05〜0.5%およびNi:0.05〜0.5%のうちから選ばれた少なくとも1種を、以下の理由で含有できる。すなわち、Mo、Cu、Niは、Mn、Si、Pと同様に固溶強化により高強度化を促進させるが、延性やr値などへは影響の小さい元素である。特に、MoはCを析出固定させて高r値化に寄与する元素でもある。これらの効果を得る上では、各々0.05%以上含有させることが好ましい。しかしながら、過剰の添加はこれらの効果を飽和させるだけでなく、合金コスト増を招くことから各々上限は0.5%とすることが好ましい。 In addition to the above component composition, at least one selected from Mo: 0.05 to 0.5%, Cu: 0.05 to 0.5%, and Ni: 0.05 to 0.5% can be contained for the following reason. That is, Mo, Cu, and Ni are elements that promote high strength by solid solution strengthening like Mn, Si, and P, but have little influence on ductility, r value, and the like. In particular, Mo is an element that contributes to increasing the r value by precipitating and fixing C. In order to obtain these effects, each content is preferably 0.05% or more. However, excessive addition not only saturates these effects, but also increases alloy costs, so each upper limit is preferably made 0.5%.
なお、Ca、REM等を通常の鋼組成範囲内であれば含有しても何ら問題はない。CaおよびREMは硫化物系介在物の形態を制御する作用を有し、これにより鋼板の局部延性などの劣化を防止する。このような効果は、CaとREMのうちから選ばれた少なくとも1種の含有量が合計で0.01%を超えると飽和するので、合計で0.01%以下とすることが好ましい。 In addition, there is no problem even if Ca, REM, etc. are contained within the normal steel composition range. Ca and REM have the effect of controlling the form of sulfide inclusions, thereby preventing the deterioration of the local ductility and the like of the steel sheet. Since such an effect is saturated when the content of at least one selected from Ca and REM exceeds 0.01% in total, it is preferable to make the total 0.01% or less.
2)平均r値が1.5以上
本発明の鋼板は、上記成分組成を満足するとともに、平均r値1.5以上を満足するものである。一方、平均r値は、次に述べる粒界を挟む2つの結晶方位差が15°以上の高傾角粒界の存在比率にも関係する。該高傾角粒界の存在比率を高めて耐二次加工脆性を改善する上では、板面垂直方向に<111>方向が向いていることが有効であり、これはr値が高いことに相当する。すなわち、該高傾角粒界の存在比率を高めて、後述するY<30を満足させる上では、平均r値が1.5以上となるような粒界を形成する必要がある。
2) Average r value of 1.5 or more The steel sheet of the present invention satisfies the above component composition and also satisfies an average r value of 1.5 or more. On the other hand, the average r value is also related to the abundance ratio of high-angle grain boundaries in which two crystal orientation differences sandwiching the grain boundaries described below are 15 ° or more. In order to improve the secondary work brittleness resistance by increasing the existence ratio of the high-angle grain boundaries, it is effective that the <111> direction is oriented perpendicular to the plate surface, which corresponds to a high r value. To do. That is, in order to increase the existence ratio of the high-angle grain boundaries and satisfy Y <30, which will be described later, it is necessary to form grain boundaries having an average r value of 1.5 or more.
3)Y(=1500XP-3[B]-1.3X)<30
粒界を挟む2つの結晶方位差が15°以上の高傾角粒界は<111>軸周りの60°回転であり、ランダムな粒界に比べて粒界での原子配列が規則的であり、粒界エネルギーが低い。ここで、Pなどの粒界偏析などには、この粒界を挟む2つの結晶方位差が15°以上の高傾角粒界のうち、特に結晶方位差が50°以上の高傾角粒界の存在比率Xが重要で、この値が大きいほど耐二次加工性は向上する。
3) Y (= 1500XP-3 [B] -1.3X) <30
A high-angle grain boundary with two crystal orientation differences of 15 ° or more across the grain boundary is rotated by 60 ° around the <111> axis, and the atomic arrangement at the grain boundary is regular compared to the random grain boundary, Low grain boundary energy. Here, in the case of grain boundary segregation such as P, there is a high-angle grain boundary having a crystal orientation difference of 50 ° or more among two high-angle grain boundaries having a crystal orientation difference of 15 ° or more sandwiching the grain boundary. The ratio X is important. The larger the value, the better the secondary workability.
また、XP(=[P](1+0.1[Si]+0.2[Mn]))は、本発者等が耐二次加工性とP、Si、Mn量との関係から求めた回帰式であり、P当量に相当するものであるが、この値が大きいほど耐二次加工性は低下する。 XP (= [P] (1 + 0.1 [Si] +0.2 [Mn])) is a regression equation obtained by the present inventors etc. from the relationship between secondary work resistance and the amounts of P, Si, and Mn. Yes, it corresponds to P equivalent, but as this value increases, the secondary work resistance decreases.
さらに、Bは、上述したように、粒界を強化し、耐二次加工脆性を向上させるので、その量[B]は本発明範囲内で多いほど好ましい。 Further, as mentioned above, B strengthens the grain boundaries and improves the secondary work brittleness resistance. Therefore, the amount [B] is preferably as large as possible within the scope of the present invention.
図1に、これらのパラメータと脆性遷移温度との関係を示したが、Y=1500XP-3[B]-1.3Xが30未満であれば、脆性遷移温度が大きく低下して-40℃以下となり、耐二次加工脆性に優れることがわかる。なお、Yが10以下であれば、脆性遷移温度が-80℃以下となり、より優れた耐二次加工脆性が得られる。ここで、脆性遷移温度は次のようにして求めた。65mm径の円板にブランキング後、33mm径の鋼球を用いてコニカルカップを作成し、これを高さ27mmとなるように耳部を切り落とし試験カップを作製した。試験カップを所定の温度まで冷やした後、5kgの錘を80cmの高さから試験カップに落とし、カップの割れの有無で遷移温度を判定した。そして、3回試験を行い3回とも割れない最低温度を脆性遷移温度とした。 Figure 1 shows the relationship between these parameters and the brittle transition temperature. If Y = 1500XP-3 [B] -1.3X is less than 30, the brittle transition temperature is greatly reduced to -40 ° C or less. It can be seen that the secondary work brittleness resistance is excellent. If Y is 10 or less, the brittle transition temperature is −80 ° C. or less, and better secondary work brittleness resistance can be obtained. Here, the brittle transition temperature was determined as follows. After blanking a 65 mm diameter disk, a 33 mm diameter steel ball was used to make a conical cup, and the ear was cut off to a height of 27 mm to make a test cup. After the test cup was cooled to a predetermined temperature, a 5 kg weight was dropped from a height of 80 cm onto the test cup, and the transition temperature was determined based on whether or not the cup was cracked. Then, the test was performed three times, and the lowest temperature at which cracking did not occur three times was defined as the brittle transition temperature.
なお、本発明の鋼板は、後述するように冷延鋼板として得ることができ、また、冷延鋼板表面にめっき層を有するめっき鋼板として得ることもできる。すなわち、本発明における鋼板は、冷延鋼板の他、冷延鋼板表面にめっき層を有するめっき鋼板も含む。 In addition, the steel plate of this invention can be obtained as a cold-rolled steel plate so that it may mention later, and can also be obtained as a plated steel plate which has a plating layer on the surface of a cold-rolled steel plate. That is, the steel plate in the present invention includes a cold-rolled steel plate and a plated steel plate having a plating layer on the surface of the cold-rolled steel plate.
4)製造方法
スラブ加熱温度:1000〜1300℃
本発明の製造方法では、まず、上記組成を有する鋼スラブ(以下、単にスラブという)を、熱間圧延に先立ち、加熱する必要がある。このとき、後述する仕上温度を確保するためにスラブ加熱温度は1000℃以上にする必要がある。また、スラブ加熱温度が1300℃を超えると加熱時のTiNや硫化物などの析出物の形成が十分でないばかりか、γ粒の粗大化や、熱エネルギーコストの増加、スケールロスの増大を引き起こすので、スラブ加熱温度は1300℃以下にする必要がある。
4) Manufacturing method Slab heating temperature: 1000-1300 ℃
In the production method of the present invention, first, a steel slab having the above composition (hereinafter simply referred to as slab) needs to be heated prior to hot rolling. At this time, the slab heating temperature needs to be 1000 ° C. or higher in order to ensure the finishing temperature described later. In addition, if the slab heating temperature exceeds 1300 ° C, not only precipitates such as TiN and sulfides are formed during heating, but also coarsening of γ grains, an increase in thermal energy costs, and an increase in scale loss. The slab heating temperature must be 1300 ° C or lower.
このとき、使用するスラブは、成分のマクロ偏析を防止すべく連続鋳造法で製造されることが望ましいが、造塊法で製造されてもよい。連続鋳造法では、薄スラブ鋳造法でもよい。また、スラブを熱間圧延するには、スラブを一旦室温まで冷却、その後再加熱して圧延する従来法に加え、室温まで冷却せず温片のままで加熱炉に装入し圧延する方法などの省エネルギープロセスも適用できる。 At this time, the slab to be used is preferably manufactured by a continuous casting method to prevent macro segregation of components, but may be manufactured by an ingot-making method. The continuous casting method may be a thin slab casting method. Moreover, in order to hot-roll the slab, in addition to the conventional method in which the slab is once cooled to room temperature and then reheated and rolled, a method in which the slab is charged in a heating furnace without being cooled to room temperature and rolled, etc. The energy saving process can also be applied.
熱間圧延の仕上温度FT:800〜950℃
加熱後のスラブは、粗圧延および仕上圧延からなる熱間圧延が施される。スラブは、粗圧延によりシートバーとされるが、粗圧延の条件は、特に規定されず、常法に従って行えばよい。なお、スラブ加熱温度を低くした場合は、圧延時のトラブルを防止するといった観点から、シートバーヒーターを活用してシートバーを加熱することが好ましい。
Hot rolling finishing temperature FT: 800 ~ 950 ℃
The heated slab is subjected to hot rolling consisting of rough rolling and finish rolling. The slab is made into a sheet bar by rough rolling, but the conditions for the rough rolling are not particularly defined, and may be performed according to a conventional method. When the slab heating temperature is lowered, it is preferable to use a sheet bar heater to heat the sheet bar from the viewpoint of preventing troubles during rolling.
シートバーは、仕上圧延により熱延鋼板とされる。このとき、FTは800〜950℃とする。これは、FTが800℃未満では、圧延負荷が大きくなり、成分によってはフェライト域圧延になり熱間圧延後の組織が粗大化し、焼鈍後に優れた深絞り性が得られず、950℃を超えると熱延鋼板の組織が粗大化し、焼鈍後に優れた深絞り性が得られないばかりか、スケール欠陥などの表面欠陥を誘発するためである。 The sheet bar is made into a hot-rolled steel sheet by finish rolling. At this time, FT shall be 800-950 degreeC. This is because when FT is less than 800 ° C, the rolling load becomes large, and depending on the component, ferrite region rolling occurs, the structure after hot rolling becomes coarse, and excellent deep drawability cannot be obtained after annealing, exceeding 950 ° C. This is because the structure of the hot-rolled steel sheet becomes coarse, and not only excellent deep drawability cannot be obtained after annealing, but also induces surface defects such as scale defects.
また、熱間圧延時の圧延荷重を低減するために、仕上圧延の一部または全部のパス間で潤滑圧延を行うこともできる。潤滑圧延時の摩擦係数は0.10〜0.25の範囲にすることが好ましい。さらに、熱間圧延の操業安定性の観点から、シートバー同士を接合して連続的に仕上圧延する連続圧延プロセスを適用することが好ましい。 Moreover, in order to reduce the rolling load at the time of hot rolling, lubrication rolling can also be performed between some or all passes of finish rolling. The coefficient of friction during lubrication rolling is preferably in the range of 0.10 to 0.25. Furthermore, from the viewpoint of operational stability of hot rolling, it is preferable to apply a continuous rolling process in which sheet bars are joined and finish-rolled continuously.
熱間圧延後の冷却条件:圧延後0.5s以内に30℃/s以上の平均冷却速度で鋼板表面温度が400℃以下になるまで冷却
本発明においては、再結晶完了前の加工組織を微細化する必要があるが、それには、圧延後0.5s内に冷却を開始する必要がある。また、γ域で未再結晶状態で圧延された組織が回復しないように、30℃/s以上の平均冷却速度で冷却する必要がある。さらに、下記に示すように550〜720℃に昇温した際にNbやTiの炭化物の生成・成長を促進させて焼鈍後に結晶方位差が50°以上の高傾角粒界の存在比率を高めるために、冷却は鋼板表面温度が400℃以下になるまで行う必要がある。
Cooling conditions after hot rolling: Cooling until the steel sheet surface temperature reaches 400 ° C or lower at an average cooling rate of 30 ° C / s or higher within 0.5 s after rolling.In the present invention, the work structure before completion of recrystallization is refined. However, it is necessary to start cooling within 0.5 s after rolling. Moreover, it is necessary to cool at an average cooling rate of 30 ° C./s or more so that the structure rolled in an unrecrystallized state in the γ region does not recover. Furthermore, to increase the existence ratio of high-angle grain boundaries whose crystal orientation difference is 50 ° or more after annealing by promoting the formation and growth of Nb and Ti carbides when heated to 550-720 ° C as shown below In addition, the cooling needs to be performed until the steel sheet surface temperature is 400 ° C. or lower.
巻取り後の鋼板表面温度:550〜720℃
上記したように、鋼板表面温度が400℃以下になるまで冷却された熱延鋼板は巻取られて鋼板コイルとなる。ここで、熱延鋼板の組織の微細化およびNbCやTiCの析出を図って高r値化するため、巻取り後の鋼板表面温度が550〜720℃であるように昇温する必要がある。昇温は、鋼板自体の復熱や変態発熱により達成してもよく、外部から加熱することによって達成してもよい。すなわち、一旦鋼板表面温度が400℃以下になるまで冷却した後、冷却を停止することで、鋼板自体の持つ熱量により復熱させ、あるいはオーステナイトからフェライト組織へ変態させて発熱させ、鋼板表面を昇温できる。こうした復熱や変態発熱によっても鋼板表面温度を550〜720℃に昇温できない場合は、さらに鋼板コイルを加熱すればよい。加熱手段としては、例えば、鋼板コイルに保熱カバーをかぶせ、該カバーを加熱する方法が挙げられる。なお、鋼板コイルに巻取られた状態では、鋼板の表面と内部との温度は均質化されるため、巻取り後の鋼板表面温度は、鋼板内部の温度と同等であり、鋼板コイル温度として求めることができる。
Steel sheet surface temperature after winding: 550-720 ° C
As described above, the hot-rolled steel sheet cooled until the steel sheet surface temperature becomes 400 ° C. or lower is wound to form a steel sheet coil. Here, in order to increase the r value by refining the microstructure of the hot-rolled steel sheet and precipitating NbC and TiC, it is necessary to raise the temperature so that the steel sheet surface temperature after winding is 550 to 720 ° C. The temperature increase may be achieved by recuperation or transformation heat generation of the steel plate itself, or may be achieved by heating from the outside. In other words, once the steel sheet surface temperature is lowered to 400 ° C. or lower, the cooling is stopped, so that heat is recovered by the amount of heat of the steel sheet itself, or transformed from austenite to a ferrite structure to generate heat, and the steel sheet surface is raised. Can be warm. If the steel sheet surface temperature cannot be raised to 550 to 720 ° C. even by such recuperation or transformation heat generation, the steel sheet coil may be further heated. Examples of the heating means include a method of covering a steel plate coil with a heat retaining cover and heating the cover. In addition, in the state wound by the steel plate coil, since the temperature of the surface and inside of a steel plate is homogenized, the steel plate surface temperature after winding is equivalent to the temperature inside a steel plate, and calculates | requires as a steel plate coil temperature. be able to.
昇温後の鋼板表面温度が550℃未満だと、炭化物の析出が不十分となり、一方、720℃を超えると、フェライト粒径が粗大となってr値が低下するので、巻取り後の鋼板表面温度は550〜720℃に昇温する必要があるが、600〜680℃に昇温することが好ましい。 If the surface temperature of the steel sheet after the temperature rise is less than 550 ° C, the precipitation of carbide becomes insufficient. On the other hand, if it exceeds 720 ° C, the ferrite grain size becomes coarse and the r value decreases, so the steel plate after winding The surface temperature needs to be raised to 550 to 720 ° C, but preferably raised to 600 to 680 ° C.
圧延率:50%以上
巻取られた熱延鋼板は、スケール除去のため酸洗を行った後、冷間圧延され、冷延鋼板とされる。このとき、冷間圧延の圧延率は、50%未満では{111}再結晶集合組織が発達せず、優れた深絞り性を得ることが困難となるので、50%以上、好ましくは60%以上にする必要がある。一方、本発明では90%までの範囲では圧延率を高くするほどr値が上昇するが、圧延率が90%を超えるとその効果が飽和するばかりでなく、圧延時のロールへの負荷も高まるため、圧延率の上限は90%とすることが好ましい。
Rolling ratio: 50% or more The hot-rolled steel sheet wound up is pickled for scale removal, and then cold-rolled into a cold-rolled steel sheet. At this time, if the rolling rate of cold rolling is less than 50%, {111} recrystallized texture does not develop, and it becomes difficult to obtain excellent deep drawability, so 50% or more, preferably 60% or more It is necessary to. On the other hand, in the present invention, in the range up to 90%, the r value increases as the rolling rate increases, but when the rolling rate exceeds 90%, not only the effect is saturated, but also the load on the roll during rolling increases. Therefore, the upper limit of the rolling rate is preferably 90%.
焼鈍の加熱条件:400〜700℃の温度範囲を15℃/s以下の平均加熱速度で加熱
その後、冷延鋼板は焼鈍されるが、結晶方位差が50°以上の高傾角粒界の存在比率を高めるには、上述した巻取り時に析出させた粒成長性を支配するNbCやTiCの炭化物と再結晶集合組織を制御する必要がある。そのためには、回復段階から再結晶初期段階である400〜700℃での加熱速度が重要であり、この温度域での加熱速度を15℃/s以下にし、高傾角粒界の存在比率を高める必要がある。
Heating conditions for annealing: Heating the temperature range of 400-700 ° C at an average heating rate of 15 ° C / s or less.Then, the cold-rolled steel sheet is annealed, but the existence ratio of high-angle grain boundaries with a crystal orientation difference of 50 ° or more In order to improve the above, it is necessary to control the carbide and recrystallization texture of NbC and TiC which control the grain growth property precipitated during the winding described above. For this purpose, the heating rate from 400 to 700 ° C, which is the initial stage of recrystallization from the recovery phase, is important. The heating rate in this temperature range is set to 15 ° C / s or less to increase the existence ratio of high-angle grain boundaries There is a need.
焼鈍温度:820〜950℃
回復段階から再結晶初期段階における加熱速度を制御した後は、820〜950℃の焼鈍で焼鈍する必要がある。これは、焼鈍温度が820℃未満では再結晶後の粒成長が不十分で、結晶方位差が50°以上の高傾角粒界の存在比率を十分に高めることができなく、950℃を超えるとγ単相での焼鈍となって、r値が低下し、結晶方位差が50°以上の高傾角粒界の存在比率も低下するためである。
Annealing temperature: 820 ~ 950 ℃
After controlling the heating rate from the recovery stage to the initial stage of recrystallization, it is necessary to anneal at 820 to 950 ° C. This is because if the annealing temperature is less than 820 ° C, the grain growth after recrystallization is insufficient, and the existence ratio of high-angle grain boundaries with a crystal orientation difference of 50 ° or more cannot be sufficiently increased. This is because the annealing in the γ single phase results in a decrease in the r value and a decrease in the existence ratio of high-angle grain boundaries having a crystal orientation difference of 50 ° or more.
焼鈍後の冷延鋼板には、電気めっき処理や溶融めっき処理などのめっき処理を施して、鋼板表面にめっき層を形成してもよい。また、めっきの種類については、例えば純亜鉛の他、亜鉛を主成分として合金元素を添加した亜鉛系めっき、あるいは純Alや、Alを主成分として合金元素を添加したAl系めっきなどが適用できる。 The cold-rolled steel sheet after annealing may be subjected to a plating process such as an electroplating process or a hot dipping process to form a plating layer on the surface of the steel sheet. In addition to pure zinc, for example, zinc-based plating in which zinc is the main component and alloying elements are added, or pure Al, Al-based plating in which Al is the main component and alloying elements can be applied. .
例えば、めっき処理として、自動車用鋼板に多く用いられる溶融亜鉛めっき処理を行う場合には、上記焼鈍を連続溶融亜鉛めっきラインにて行い、焼鈍後引き続いて溶融亜鉛めっき浴に浸漬し、鋼板表面に溶融亜鉛めっき層を形成すればよい。さらに、合金化処理を行い、合金化溶融亜鉛めっき鋼板としてもよい。 For example, when performing hot dip galvanizing treatment often used for automobile steel plates as plating treatment, the annealing is performed in a continuous hot dip galvanizing line, and after immersion, immersed in a hot dip galvanizing bath, A hot dip galvanized layer may be formed. Further, alloying treatment may be performed to obtain an alloyed hot-dip galvanized steel sheet.
このようにして製造された冷延鋼板、さらにはめっき処理を施しためっき鋼板には、形状矯正、表面粗度調整等の目的で調質圧延またはレベラー加工を施すこともできる。この調質圧延またはレベラー加工の伸び率は0.2〜15%の範囲とすることが好ましい。0.2%未満では形状矯正、表面粗度調整の目的が達成できず、15%を超えると顕著な延性の低下を招く。なお、より好ましくは2%以下である。調質圧延とレベラー加工では加工形式が相違するが、その効果は両者で大きな差がないことを確認している。そして、これらの調質圧延およびレベラー加工はめっき処理後でも有効である。 The cold-rolled steel sheet thus manufactured, and further the plated steel sheet subjected to the plating treatment, can be subjected to temper rolling or leveler processing for the purpose of shape correction, surface roughness adjustment, and the like. The elongation of the temper rolling or leveler processing is preferably in the range of 0.2 to 15%. If it is less than 0.2%, the purpose of shape correction and surface roughness adjustment cannot be achieved, and if it exceeds 15%, the ductility is remarkably lowered. More preferably, it is 2% or less. It has been confirmed that there is no significant difference in the effect between temper rolling and leveler processing, although the processing formats are different. These temper rolling and leveler processing are effective even after the plating treatment.
表1に示す組成の鋼A〜Lを転炉で溶製し、連続鋳造法でスラブとした。これらスラブを1250℃に加熱後、粗圧延してシートバーとし、次いで表2に示す熱延条件で熱延鋼板とした。なお、表2に示す鋼板コイル温度は、熱間圧延後巻取った鋼板コイルに保熱カバーをかぶせた上で、加熱することにより達成した。これらの熱延鋼板を酸洗後圧延率65%で冷間圧延して冷延鋼板(板厚:1.2mm)とし、引き続き、連続焼鈍ラインにて表2に示す焼鈍条件で焼鈍を行い、伸び率0.5%の調質圧延を施して鋼板No.1〜26の試料を作製した。なお、鋼板No.2は、連続溶融亜鉛めっきラインにて連続焼鈍を施し、その後引き続きインラインで溶融亜鉛めっき(めっき浴温:480℃)を施した溶融亜鉛めっき鋼板である。そして、得られた試料について、引張特性値、r値、耐二次加工脆性、結晶方位差が50°以上の高傾角粒界の存在比率の測定、評価を以下の方法で行った。 Steels A to L having the compositions shown in Table 1 were melted in a converter and made into slabs by a continuous casting method. These slabs were heated to 1250 ° C., roughly rolled into sheet bars, and then hot-rolled steel sheets under the hot-rolling conditions shown in Table 2. The steel plate coil temperatures shown in Table 2 were achieved by heating a steel plate coil wound after hot rolling with a heat insulating cover covered. These hot-rolled steel sheets are pickled and cold-rolled at a rolling rate of 65% to form cold-rolled steel sheets (thickness: 1.2 mm), and subsequently subjected to annealing under the annealing conditions shown in Table 2 in a continuous annealing line. A sample of steel plates Nos. 1 to 26 was prepared by temper rolling at a rate of 0.5%. Steel plate No. 2 is a hot dip galvanized steel plate that has been subjected to continuous annealing in a continuous hot dip galvanizing line, and subsequently hot dip galvanized (plating bath temperature: 480 ° C.). And about the obtained sample, the measurement of the tensile characteristic value, r value, secondary work brittleness resistance, and the existence ratio of the high-angle grain boundary having a crystal orientation difference of 50 ° or more were performed and evaluated by the following methods.
引張特性:試料から圧延方向に対して90°方向にJIS5号引張試験片を採取し、JIS Z 2241の規定に準拠してクロスヘッド速度10mm/minで引張試験を行い、降伏強度YS、TS、伸びElを求めた。 Tensile properties: JIS No. 5 tensile test specimen is taken from the sample at 90 ° direction with respect to the rolling direction, tensile test is performed at a crosshead speed of 10 mm / min in accordance with the provisions of JIS Z 2241, yield strength YS, TS, The elongation El was obtained.
r値:試料から圧延方向、圧延方向に対し45°方向、圧延方向に対し90°方向からJIS5号引張試験片を採取し、10%の単軸引張歪を付与した時の各試験片の幅歪と板厚歪を測定し、JIS Z 2254の規定に準拠して平均のr値(平均塑性歪比)を次の式から算出し、深絞り性を評価した。
r値=(r0+2r45+r90)/4
ここで、r0、r45、r90は、それぞれ圧延方向に対し0°、45°、90°方向から採取した試験片で測定した塑性歪比である。
r value: JIS No. 5 tensile test specimen taken from the sample in the rolling direction, 45 ° direction to the rolling direction, and 90 ° direction to the rolling direction, and the width of each test piece when 10% uniaxial tensile strain was applied. Strain and plate thickness strain were measured, and an average r value (average plastic strain ratio) was calculated from the following formula in accordance with the provisions of JIS Z 2254 to evaluate deep drawability.
r value = (r 0 + 2r 45 + r 90 ) / 4
Here, r 0, r 45, and r 90 are plastic strain ratios measured with test pieces taken from 0 °, 45 °, and 90 ° directions with respect to the rolling direction, respectively.
耐二次加工脆性:65mm径の円板にブランキング後、33mm径の鋼球を用いてコニカルカップを作成し、これを高さ27mmとなるように耳部を切り落とし試験カップを作製した。試験カップを所定の温度まで冷やした後、5kgの錘を80cmの高さから試験カップに落とし、カップの割れの有無で遷移温度を判定した。そして、3回試験を行い3回とも割れない最低温度を脆性遷移温度とし、耐二次加工脆性を評価した。 Secondary processing brittleness resistance: After blanking on a 65 mm diameter disc, a conical cup was prepared using a 33 mm diameter steel ball, and the ear was cut off to a height of 27 mm to prepare a test cup. After the test cup was cooled to a predetermined temperature, a 5 kg weight was dropped from a height of 80 cm onto the test cup, and the transition temperature was determined based on whether or not the cup was cracked. Then, the test was performed three times, and the lowest temperature at which cracking did not occur three times was regarded as the brittle transition temperature, and the secondary work brittleness resistance was evaluated.
結晶方位差が50°以上の高傾角粒界の存在比率X:EBSD(Electron Back-Scatter Diffraction)にて、500μm×500μmの視野を3視野測定し、粒界を挟む2つの結晶方位差を解析し、結晶方位差が15°以上の粒界のうち、結晶方位差が50°以上の粒界の割合を算出した。 The existence ratio of high-angle grain boundaries with a crystal orientation difference of 50 ° or more X: EBSD (Electron Back-Scatter Diffraction) is used to measure three fields of view of 500 μm × 500 μm and analyze two crystal orientation differences across the grain boundary The ratio of grain boundaries having a crystal orientation difference of 50 ° or more out of the grain boundaries having a crystal orientation difference of 15 ° or more was calculated.
結果を表2に示す。本発明例では、いずれもTSが340MPa以上、r値が1.5以上で、脆性遷移温度も-40℃以下で低く耐二次工脆性が優れていることがわかる。 The results are shown in Table 2. In the examples of the present invention, TS is 340 MPa or more, r value is 1.5 or more, brittle transition temperature is -40 ° C. or less, and it is understood that secondary work brittleness resistance is excellent.
Claims (4)
Y=1500XP-3[B]-1.3X・・・(1)
ここで、XP=[P](1+0.1[Si]+0.2[Mn])で、Xは粒界を挟む2つの結晶方位差が15°以上の高傾角粒界のうち結晶方位差が50°以上の高傾角粒界の存在比率(%)を表し、[M]は元素Mの含有量(質量%、ただし[B]はppm)を表す。 In mass%, C: 0.0005 to 0.04%, Si: 0.01 to 1.0%, Mn: 0.2 to 3%, P: 0.003 to 0.15%, S: 0.015% or less, Al: 0.005 to 0.5%, N: 0.006% or less B: 0.0003 to 0.01%, and Nb: 0.003 to 0.1% and Ti: at least one selected from 0.003 to 0.1%, and the balance has a composition consisting of Fe and inevitable impurities, A high-strength steel sheet having an average r value of 1.5 or more and Y defined by the following formula (1) being less than 30;
Y = 1500XP-3 [B] -1.3X ... (1)
Here, XP = [P] (1 + 0.1 [Si] +0.2 [Mn]), and X is a high-angle grain boundary between two crystal orientation differences of 15 ° or more sandwiching the grain boundary, the crystal orientation difference is 50 It represents the abundance (%) of high-angle grain boundaries at or above °, and [M] represents the content of element M (mass%, [B] is ppm).
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