JP6068570B2 - Annealing process for high strength steel sheet - Google Patents
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本発明は、鋼板の焼きなましプロセスに関し、特に高強度鋼板の焼きなましプロセスに関する。 The present invention relates to a steel plate annealing process, and more particularly to a high strength steel plate annealing process.
近年、省エネルギー・低炭素化の要求が高まるにつれて、燃料消費量を削減することで省エネルギー・低炭素化の目標を達成するために、自動車産業界では車体の軽量化に向けて力を入れている。車体を軽量化するための有効な手段として車体用鋼板の薄肉化が知られているが、鋼板を薄肉化する一方で、車体の安全性を維持しなければならず、したがって、車用鋼板の強度を向上しなければならない。更に、車用鋼板の強度と鋼板の延性を両立させるために、高強度・高延性の車用鋼板を開発する必要がある。 In recent years, as the demand for energy saving and carbon reduction has increased, the automobile industry is making efforts to reduce the weight of the vehicle body in order to achieve the goal of energy saving and carbon reduction by reducing fuel consumption. . Although it is known to reduce the thickness of the steel plate for the vehicle body as an effective means for reducing the weight of the vehicle body, it is necessary to maintain the safety of the vehicle body while reducing the thickness of the steel plate. Strength must be improved. Furthermore, in order to achieve both the strength of the steel plate for automobiles and the ductility of the steel plate, it is necessary to develop a high strength and high ductility automotive steel plate.
過去数年、鉄鋼産業では所謂第一世代（１ｓｔ ｇｅｎｅｒａｔｉｏｎ）及び第二世代（２ｎｄ ｇｅｎｅｒａｔｉｏｎ）の車用高強度鋼（ａｄｖａｎｃｅｄ ｈｉｇｈ ｓｔｒｅｎｇｔｈ ｓｔｅｅｌ，ＡＨＳＳ）が開発されている。第一世代の車用高強度鋼は、主に変態誘起塑性鋼（ＴＲＩＰ−ａｓｓｉｓｔｅｄ ｓｔｅｅｌｓ）を指し、その引張強度が約６００〜１０００ＭＰａである一方で、伸び率が２０〜４０％であり、抗張積（即ち引張強度と伸び率との積）が２０ＧＰａ％未満である。変態誘起塑性鋼の引張強度及び伸び率が自動車産業界の要求より低いため、第二世代の車用高強度鋼が開発された。 In the past few years, the steel industry has developed so-called 1st generation and 2nd generation advanced high strength steel (AHSS). The first-generation high-strength steel for vehicles mainly refers to TRIP-assisted steels, and its tensile strength is about 600 to 1000 MPa, while its elongation is 20 to 40%, The tension (that is, the product of tensile strength and elongation) is less than 20 GPa%. Due to the lower tensile strength and elongation of transformation-induced plastic steel than required by the automotive industry, a second generation high strength steel for vehicles was developed.
第二世代の車用高強度鋼は、主に双晶誘起塑性鋼（ＴＷＩＰ ｓｔｅｅｌｓ）を指し、高マンガン合金鋼であり、そのマンガン含有量は約２０〜３０ｗｔ％である。双晶誘起塑性鋼は極めて優れた強度を有し、その引張強度が約６００〜１１００ＭＰａで、６０〜９５％の伸び率を保つことができるため、抗張積が６０ＧＰａ％までに達し得る。双晶誘起塑性鋼は既に１０年近く発展してきたが、自動車産業界に受け入れられておらず、その要因として、必要なマンガン含有量が非常に高いので、コスト面から好ましくないことにある。 The second-generation high-strength steel for vehicles mainly refers to twinning induced plastic steel (TWIP steels), is a high manganese alloy steel, and its manganese content is about 20-30 wt%. The twinning-induced plastic steel has extremely excellent strength, its tensile strength is about 600-1100 MPa, and can maintain an elongation of 60-95%, so that the tensile product can reach up to 60 GPa%. Although twin-induced plastic steel has already been developed for nearly 10 years, it has not been accepted by the automobile industry, and the factor is that the required manganese content is very high, which is undesirable from a cost standpoint.
第一世代の車用高強度鋼は抗張積が低すぎて、車用鋼板に求められる性質を満足できず、また第二世代の車用高強度鋼は、マンガン合金の使用量が高すぎるので、コストから好ましくないため、自動車産業界では、第三世代の車用高強度鋼の開発に取り組んでいる。 The first-generation high-strength steel for cars is too low in tensile strength to satisfy the properties required for automotive steel plates, and the second-generation high-strength steel for cars uses too much manganese alloy Therefore, because it is not preferable from the cost, the automobile industry is working on the development of high-strength steel for third-generation vehicles.
図１は、第三世代の車用高強度鋼の目標性質範囲図を示す。図１に示されるように、第三世代の車用高強度鋼は、抗張積が約２０〜４０ＧＰａ％である。しかしながら、自動車産業界では、第三世代の車用高強度鋼の製造方法はまだ開発段階に留まっており、特に、如何に鋼板の焼きなましプロセスを設計すれば、鋼板が目標抗張積に達し得るかが、今日の自動車産業界において非常に重要な課題となっている。 FIG. 1 shows a target property range diagram of a third-generation high-strength steel for vehicles. As shown in FIG. 1, the third-generation high-strength steel for vehicles has a tensile product of about 20 to 40 GPa%. However, in the automotive industry, the third-generation high-strength steel production methods are still in the development stage, especially if the steel sheet annealing process is designed, the steel sheet can reach the target tensile product. However, it is a very important issue in today's automobile industry.
したがって、第三世代の車用高強度鋼に要求される性質を満足できる鋼板を製造することができるように、革新的で進歩性を備えた高強度鋼板の焼きなましプロセスを提供することが必要である。 Therefore, it is necessary to provide an innovative and inventive annealing process for high-strength steel sheets so that steel sheets that satisfy the properties required for third-generation high-strength steels for vehicles can be manufactured. is there.
本発明は、０．１−０．４質量％の炭素、１−３質量％のマンガン、１−２質量％のケイ素、０．１−０．２質量％のチタン、及び残部の鉄と不可避的不純物からなる組成を有する合金鋼板を提供するステップと、該合金鋼板にオーステナイト相が形成するように、該合金鋼板をオーステナイト生成温度に加熱するステップと、該合金鋼板に界面ナノ析出物及びフェライト相が形成するように、該合金鋼板をフェライト生成温度に冷却するステップと、該合金鋼板にベイナイト相が形成するように、該合金鋼板をベイナイト生成温度に冷却するステップと、複相微細組織を有する高強度鋼板が製造されるように、該合金鋼を常温に冷却するステップと、を含む高強度鋼板の焼きなましプロセスを提供する。 The present invention relates to 0 . 1-0.4 wt% carbon, 1-3 wt% manganese, 1-2 wt% silicon, 0.1-0.2 wt% of titanium, and with balance of iron and unavoidable impurities Providing an alloy steel sheet, heating the alloy steel sheet to an austenite formation temperature so that an austenite phase is formed in the alloy steel sheet, and forming interfacial nanoprecipitates and a ferrite phase in the alloy steel sheet. A step of cooling the alloy steel sheet to a ferrite forming temperature; a step of cooling the alloy steel sheet to a bainite forming temperature so that a bainite phase is formed in the alloy steel sheet; and a high-strength steel sheet having a multiphase microstructure is manufactured. And cooling the alloy steel to room temperature, and providing an annealing process for the high strength steel sheet.
本発明の焼きなましプロセスによれば、引張強度が８１５ＭＰａで、伸び率が２６％で、抗張積が２１．２ＧＰａ％である高強度鋼板を製造することができ、このような鋼板の性質は第三世代の車用高強度鋼に要求される性質を満たす。 According to the annealing process of the present invention, a high-strength steel sheet having a tensile strength of 815 MPa, an elongation of 26%, and a tensile product of 21.2 GPa% can be produced. It meets the properties required for three-generation high-strength steel for vehicles.
本発明の技術的構成をより明確に理解し、明細書の内容に従って実施することができるようにするために、且つ本発明の上述した目的、特徴及び利点をより明確で容易に理解することができるようにするために、以下に好ましい実施例を意図的に挙げて、図面を参照しながら、次のように詳細に説明する。 To more clearly understand the technical configuration of the present invention and to be able to carry out according to the contents of the specification, and to more clearly and easily understand the above-described objects, features, and advantages of the present invention. In order to be able to do so, a preferred embodiment will be described below in detail and will be described in detail with reference to the drawings.
図２は本発明の高強度鋼板の焼きなましプロセスのフローチャートを示す。図２のステップＳ２１に示すように、成分として、０．１−０．４質量％の炭素、１−３質量％のマンガン、１−２質量％のケイ素、０．１−０．２質量％のチタン、及び残部の鉄と不可避的不純物を含む合金鋼板を提供する。このステップでは、０．１−０．４質量％の炭素によって、鋼板強化及び残留オーステナイトの量を変更して、鋼板の伸び率を増加させることができる。１−３質量％のマンガンによって、鋼板の硬化能力を向上させ、焼きなまし時の冷却速度を低下させ、かつ冷却速度のプロセス条件を緩和することができる。１−２質量％のケイ素によって、ベイナイト相でのセメンタイト炭化物の生成を抑制して、鋼板の延性を高め、また固溶強化により鋼板の強度を高めることができる。０．１−０．２質量％のチタンによって、界面ナノ析出チタン炭化物を生成して、鋼板を強化する。あるいは、ほかの実施例において、バナジウム、ニオビウム、モリブデンまたはタングステンでチタンを置換してもよい。 FIG. 2 shows a flowchart of the annealing process of the high strength steel sheet of the present invention. As shown in step S21 of FIG. 2, 0.1-0.4% by mass of carbon, 1-3% by mass of manganese, 1-2% by mass of silicon, 0.1-0.2% by mass as components . An alloy steel sheet containing titanium and the balance iron and inevitable impurities is provided. In this step, the steel sheet reinforcement and the amount of retained austenite can be changed with 0.1-0.4 mass % carbon to increase the elongation of the steel sheet. With 1-3% by mass of manganese, the hardening ability of the steel sheet can be improved, the cooling rate during annealing can be reduced, and the process conditions of the cooling rate can be relaxed. By 1-2 mass % of silicon, the production | generation of the cementite carbide in a bainite phase can be suppressed, the ductility of a steel plate can be improved, and the strength of a steel plate can be improved by solid solution strengthening. 0.1-0.2 mass % titanium produces interfacial nano-deposited titanium carbide to strengthen the steel sheet. Alternatively, in other examples, titanium may be replaced with vanadium, niobium, molybdenum, or tungsten.
また、このステップにおいて、圧延板を形成するように、該合金鋼板を熱間圧延または冷間圧延してもよい。 In this step, the alloy steel plate may be hot-rolled or cold-rolled so as to form a rolled plate.
ステップＳ２２に示すように、該合金鋼板をオーステナイト生成温度に加熱して、該合金鋼板にオーステナイト相を形成させる。本実施例において、オーステナイト生成温度は８００〜１１００℃で、保温時間は６０〜３００秒である。 As shown in step S22, the alloy steel plate is heated to an austenite generation temperature to form an austenite phase on the alloy steel plate. In this example, the austenite generation temperature is 800 to 1100 ° C., and the heat retention time is 60 to 300 seconds.
ステップＳ２３に示すように、該合金鋼板をフェライト生成温度に冷却して、該合金鋼板に界面ナノ析出物及びフェライト相を形成させる。このステップにおいて、好ましくは、冷却速度は５〜４０℃／秒で、フェライト生成温度は５８０〜７５０℃で、且つ保温時間は６０秒以下である。また、このステップで形成された界面ナノ析出物はチタン炭化物である。 As shown in step S23, the alloy steel sheet is cooled to a ferrite formation temperature to form interfacial nano precipitates and a ferrite phase on the alloy steel sheet. In this step, preferably, the cooling rate is 5 to 40 ° C./second, the ferrite formation temperature is 580 to 750 ° C., and the heat retention time is 60 seconds or less. Moreover, the interface nanoprecipitate formed in this step is titanium carbide.
ステップＳ２４に示すように、該合金鋼板をベイナイト生成温度に冷却して、該合金鋼板にベイナイト相を形成させる。このステップにおいて、好ましくは、冷却速度は５〜４０℃／秒で、ベイナイト生成温度は３００〜５００℃で、且つ保温時間は３００秒以下である。 As shown in step S24, the alloy steel plate is cooled to a bainite forming temperature to form a bainite phase on the alloy steel plate. In this step, preferably, the cooling rate is 5 to 40 ° C./second, the bainite formation temperature is 300 to 500 ° C., and the heat retention time is 300 seconds or less.
ステップＳ２５に示すように、該合金鋼板を常温に冷却して、複相顕微鏡組織を有する高強度鋼板を製造する。このステップにおいて、好ましくは、冷却速度は０．５〜４０℃／秒であり、前記複相顕微鏡組織は６０〜８０％のフェライト相、２０％以下のベイナイト相、４０％以下の残留オーステナイト相及び２０％以下のマルテンサイト相を含む。 As shown in step S25, the alloy steel plate is cooled to room temperature to produce a high-strength steel plate having a multiphase microstructure. In this step, preferably, the cooling rate is 0.5 to 40 ° C./second, and the double phase microstructure has 60 to 80% ferrite phase, 20% or less bainite phase, 40% or less residual austenite phase, and Contains a martensite phase of 20% or less.
以下、実施例により本発明を詳細に説明するが、本発明はこれらの実施例に開示された内容に制限されるものではない。 EXAMPLES Hereinafter, although an Example demonstrates this invention in detail, this invention is not restrict | limited to the content disclosed by these Examples.
図３は、本発明の昇温速度が５℃／秒である場合のＡｃ１（鋼板加熱時のオーステナイト形成開始温度）及びＡｃ３（鋼板加熱時のフェライトの完全オーステナイト化温度）の温度測定曲線を示す。図４（ａ）及び（ｂ）はそれぞれ本発明の鋼板の２階段における温度−時間−相変態曲線及び連続冷却相変態曲線を示す。 FIG. 3 shows temperature measurement curves of Ac1 (austenite formation start temperature when heating the steel sheet) and Ac3 (complete austenite forming temperature of ferrite when heating the steel sheet) when the temperature increase rate of the present invention is 5 ° C./second. . 4 (a) and 4 (b) show a temperature-time-phase transformation curve and a continuous cooling phase transformation curve in two steps of the steel sheet of the present invention, respectively.
本発明は、鉄、０．１１質量％の炭素、１．５質量％のマンガン、１．４４質量％のケイ素、０．１質量％のチタンを含む合金鋼板を例とするものであり、図３で、完全オーステナイト化温度が９７０℃と示されているが、更に鋼板の完全オーステナイト化を保つために、オーステナイト化及び析出物の固溶化温度を１０００〜１１００℃にする。オーステナイト化した後、２０℃／秒の冷却速度で鋼板を図４に示されるフェライト形成温度域（即ち５８０〜７５０℃の範囲）に冷却して、温度が低いほど、オーステナイトからフェライトへの相変態時間が長くなるため、フェライトが生成する時に界面ナノ析出物が析出する強化効果を有する。 The present invention exemplifies an alloy steel plate containing iron, 0.11% by mass of carbon, 1.5% by mass of manganese, 1.44% by mass of silicon, and 0.1% by mass of titanium. 3 shows that the complete austenitizing temperature is 970 ° C. In order to further maintain the complete austenitizing of the steel sheet, the austenitizing and precipitation solid solution temperatures are set to 1000 to 1100 ° C. After austenitization, the steel sheet was cooled to a ferrite formation temperature range shown in FIG. 4 (that is, a range of 580 to 750 ° C.) at a cooling rate of 20 ° C./second, and the lower the temperature, the phase transformation from austenite to ferrite Since the time becomes longer, it has the strengthening effect that the interface nanoprecipitate precipitates when ferrite is formed.
図５は、実施例の焼きなましプロセスの温度−時間曲線図を示す。図５を例として、フェライトの恒温形成温度を６００℃にし、且つ１２〜２２秒保温して、約７０％の界面ナノ析出により強化されたフェライト組織を得る。次に、ベイナイト相変態領域（４５０℃）まで冷却して２００秒保温し、最後にさらに常温まで冷却して、フェライト、ベイナイト及びオーステナイトの複相相変態を強化させ、残留オーステナイトが材料塑性変形時に新生マルテンサイトに変態されて、応力誘起相変態により鋼板の延性を向上させる。 FIG. 5 shows a temperature-time curve diagram of the annealing process of the example. Taking FIG. 5 as an example, the constant temperature formation temperature of ferrite is 600 ° C. and the temperature is kept for 12 to 22 seconds to obtain a ferrite structure reinforced by about 70% interfacial nanoprecipitation. Next, it is cooled to a bainite phase transformation region (450 ° C.) and kept for 200 seconds. Finally, it is further cooled to room temperature to reinforce the multiphase transformation of ferrite, bainite and austenite, and the residual austenite is deformed during material plastic deformation. It is transformed into new martensite and the ductility of the steel sheet is improved by stress-induced phase transformation.
図６は、実施例の鋼板の顕微鏡組織写真を示す。図７は、実施例の鋼板のフェライト内の炭化チタンナノ析出物の顕微鏡写真を示す。 FIG. 6 shows a micrograph of the steel sheet of the example. FIG. 7 shows a photomicrograph of titanium carbide nanoprecipitates in the ferrite of the steel sheet of the example.
図６及び図７に示すように、該鋼板の顕微鏡組織は、７０％のフェライト、１５％のベイナイト、１２％のマルテンサイト及び３％の残留オーステナイトを含む複相顕微鏡組織であり、鋼板の伸び率（Ｅｌ）を２６％まで向上させることができ、図７に示される炭化チタンナノ析出物がフェライトを強化させて、更に鋼板の引張強度を８１５ＭＰａまで向上させることができる。また、その抗張積は２１．２ＧＰａ％に達し得る。 As shown in FIGS. 6 and 7, the microstructure of the steel sheet is a multiphase microstructure containing 70% ferrite, 15% bainite, 12% martensite and 3% retained austenite, and the elongation of the steel sheet. The rate (El) can be improved to 26%, and the titanium carbide nanoprecipitates shown in FIG. 7 can strengthen the ferrite and further improve the tensile strength of the steel sheet to 815 MPa. Also, its tensile product can reach 21.2 GPa%.
図８は、実施例の鋼板の目標性質範囲図を示す。図８に示されるように、実施例の鋼板の性質は第三世代の車用高強度鋼に要求される性質を満たす。 FIG. 8 shows a target property range diagram of the steel plate of the example. As shown in FIG. 8, the properties of the steel plates of the examples satisfy the properties required for the third-generation high-strength steel for vehicles.
上記実施例は、本発明の原理及びその効果を説明するためのものに過ぎず、本発明を限定するものではない。そのため、当業者が上記実施例に対して行う修正や変更も本発明の趣旨から逸脱するものではない。本発明の請求の範囲は後述する請求の範囲に記載されたとおりである。 The above embodiments are merely for explaining the principle of the present invention and its effects, and do not limit the present invention. Therefore, modifications and changes made by those skilled in the art to the above-described embodiments do not depart from the spirit of the present invention. The claims of the present invention are as described in the claims to be described later.
Ａｃ１ 鋼板加熱時のオーステナイト形成開始温度
Ａｃ３ 鋼板加熱時のフェライトの完全オーステナイト化温度
Ｓ２１〜Ｓ２５ ステップ
Ac1 Austenite formation start temperature when heating steel plate Ac3 Complete austenitization temperature of ferrite when heating steel plate S21 to S25
Claims (2)
（ａ）０．１−０．４質量％の炭素、１−３質量％のマンガン、１−２質量％のケイ素、０．１−０．２質量％のチタン、及び残部の鉄と不可避的不純物からなる組成を有する合金鋼板を提供するステップと、
（ｂ）前記合金鋼板にオーステナイト相が形成するように、前記合金鋼板をオーステナイト生成温度に加熱するステップと、
（ｃ）前記合金鋼板に界面ナノ析出物及びフェライト相が形成するように、前記合金鋼板をフェライト生成温度に冷却するステップと、
（ｄ）前記合金鋼板にベイナイト相が形成するように、前記合金鋼板をベイナイト生成温度に冷却するステップと、
（ｅ）複相微細組織を有する高強度鋼板が製造されるように、前記合金鋼板を常温に冷却するステップと、を含み、
ステップ（ｂ）において、オーステナイト生成温度が８００〜１１００℃であり、保温時間が６０〜３００秒であり、
ステップ（ｃ）において、冷却速度が５〜４０℃／秒であり、フェライト生成温度が５８０〜７５０℃であり、保温時間が１２〜６０秒であり、界面ナノ析出物がチタン炭化物であり、
ステップ（ｄ）において、冷却速度が５〜４０℃／秒であり、ベイナイト生成温度が３００〜５００℃であり、保温時間が３００秒以下であり、
ステップ（ｅ）において、冷却速度が０．５〜４０℃／秒であり、複相微細組織が面積率で、６０〜８０％のフェライト相、２０％以下のベイナイト相、４０％以下の残留オーステナイト相及び２０％以下のマルテンサイト相を含み、
各ステップを（ａ）〜（ｅ）の順に行う、高強度鋼板の焼きなましプロセス。 An annealing process for high-strength steel sheets,
(A ) 0 . 1-0.4 wt% carbon, 1-3 wt% manganese, 1-2 wt% silicon, 0.1-0.2 wt% of titanium, and with balance of iron and unavoidable impurities Providing an alloy steel plate having ;
(B) heating the alloy steel plate to an austenite generation temperature so that an austenite phase is formed in the alloy steel plate;
(C) cooling the alloy steel sheet to a ferrite formation temperature so that interfacial nanoprecipitates and a ferrite phase are formed in the alloy steel sheet;
(D) cooling the alloy steel sheet to a bainite forming temperature so that a bainite phase is formed in the alloy steel sheet;
As (e) high-strength steel sheet having a dual phase microstructure is produced, it viewed including the steps of: cooling the alloy steel plate to room temperature,
In step (b), the austenite generation temperature is 800 to 1100 ° C., the heat retention time is 60 to 300 seconds,
In step (c), the cooling rate is 5 to 40 ° C./second, the ferrite formation temperature is 580 to 750 ° C., the heat retention time is 12 to 60 seconds, and the interface nanoprecipitate is titanium carbide,
In step (d), the cooling rate is 5 to 40 ° C./second, the bainite generation temperature is 300 to 500 ° C., and the heat retention time is 300 seconds or less,
In step (e), the cooling rate is 0.5 to 40 ° C./second, the multiphase microstructure is area ratio, 60 to 80% ferrite phase, 20% or less bainite phase, 40% or less residual austenite Phase and 20% or less martensite phase,
An annealing process for high-strength steel sheets in which each step is performed in the order of (a) to (e) .
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