TWI659113B - Hot stamping - Google Patents
Hot stamping Download PDFInfo
- Publication number
- TWI659113B TWI659113B TW107105780A TW107105780A TWI659113B TW I659113 B TWI659113 B TW I659113B TW 107105780 A TW107105780 A TW 107105780A TW 107105780 A TW107105780 A TW 107105780A TW I659113 B TWI659113 B TW I659113B
- Authority
- TW
- Taiwan
- Prior art keywords
- less
- hot
- plate thickness
- surface layer
- hardness
- Prior art date
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Classifications
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
- B21D22/02—Stamping using rigid devices or tools
- B21D22/022—Stamping using rigid devices or tools by heating the blank or stamping associated with heat treatment
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
- B21D22/20—Deep-drawing
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D—WORKING OR PROCESSING OF SHEET METAL OR METAL TUBES, RODS OR PROFILES WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21D22/00—Shaping without cutting, by stamping, spinning, or deep-drawing
- B21D22/20—Deep-drawing
- B21D22/26—Deep-drawing for making peculiarly, e.g. irregularly, shaped articles
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/011—Layered products comprising a layer of metal all layers being exclusively metallic all layers being formed of iron alloys or steels
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/04—Layered products comprising a layer of metal comprising metal as the main or only constituent of a layer, which is next to another layer of the same or of a different material
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/04—Layered products comprising a layer of metal comprising metal as the main or only constituent of a layer, which is next to another layer of the same or of a different material
- B32B15/043—Layered products comprising a layer of metal comprising metal as the main or only constituent of a layer, which is next to another layer of the same or of a different material of metal
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/18—Layered products comprising a layer of metal comprising iron or steel
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/02—Hardening articles or materials formed by forging or rolling, with no further heating beyond that required for the formation
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C21D1/62—Quenching devices
- C21D1/673—Quenching devices for die quenching
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/005—Modifying the physical properties by deformation combined with, or followed by, heat treatment of ferrous alloys
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/041—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing involving a particular fabrication or treatment of ingot or slab
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- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0426—Hot rolling
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0436—Cold rolling
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
- C21D8/0463—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment following hot rolling
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- C—CHEMISTRY; METALLURGY
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
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- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
- C21D9/48—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals deep-drawing sheets
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
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- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
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- C23C2/06—Zinc or cadmium or alloys based thereon
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Abstract
本發明提供一種熱壓印成形體,其包含板厚中央部與配置於板厚中央部的兩側或單側之表層,且該熱壓印成形體之特徵在於:該熱壓印成形體更包含中間層,該中間層係形成於板厚中央部及各表層之間且與該等相鄰接;板厚中央部具有預定之組成,板厚中央部之硬度為500Hv以上且800Hv以下;表層之板厚方向的硬度變化ΔH1
為10Hv以上且小於200Hv;中間層之板厚方向的硬度變化ΔH2
為50Hv以上且小於200Hv。
Description
本發明是有關於使用於需要強度之汽車或構造物之構造構件或補強構件的高強度鋼板,尤其是有關於耐撞擊特性及耐氫脆化特性優異之熱壓印成形體。
背景技術 近年,由環境保護及省資源化的觀點來看不斷地要求汽車車體之輕量化,因此將高強度鋼板應用於汽車用構件的情況持續加速。然而,伴隨著鋼板的高強度化,成形性卻會劣化,因此在高強度鋼板中,對複雜形狀之構件的成形性就成了課題。
為了解決上述課題,在將鋼板加熱至沃斯田鐵區之高溫後實施壓製成形之熱壓印的應用正在進展。由於熱壓印是與壓製加工同時在模具內實施淬火處理,因此可獲得對應鋼板之C量的強度,且作為兼顧汽車用構件之成形與強度確保的技術而受到矚目。
然而,藉由壓製淬火而製造之以往的熱壓製零件,由於整個板厚區域為硬質組織(主要為麻田散鐵)所形成,因此當汽車撞擊時一旦產生彎曲變形,便會在零件之翹曲部位產生最大的應變,且破裂會以鋼板之表層附近為起點進展,最終會容易斷裂。此外,由於鋼板之表層的晶格缺陷密度高所以會促進氫的侵入,而有構件之耐氫脆化特性變得貧乏的問題。因上述理由,藉由壓製淬火而製造之熱壓製零件,對汽車零件的應用部位在過去是被限定的。
對於上述問題,提案有一種提高熱壓製零件之變形能力以抑制破裂的技術。專利文獻1中揭示了將熱壓製零件之板厚中央的硬度設為400Hv以上,且另一方面於表層形成厚度20μm以上且200μm以下且硬度300Hv以下的軟質層,藉此來確保拉伸強度1300MPa以上的強度,並抑制汽車撞擊時的破裂。而且,專利文獻1中揭示了上述軟質層具有回火組織。
專利文獻2中揭示了藉由將高強度汽車構件之表層的碳濃度控制在內層鋼之碳濃度的1/5以下,以減低表層之晶格缺陷的密度並改善耐氫脆性。
專利文獻3中揭示有令鋼組織為肥粒鐵與麻田散鐵的多相組織,並將表層部之肥粒鐵面積率提高至比內層部高,以藉此獲得具有高拉伸強度、優異延展性及優異彎曲性的熱壓鋼板構件。
然而,專利文獻1及專利文獻2所記載之構件,由於是令板厚之表層部為軟質組織,並以硬質組織構成板厚之中央部,而導致在板厚方向上產生急遽的硬度梯度。因此,在受到彎曲變形時,會有在產生急遽之硬度梯度的軟質組織及硬質組織的邊界附近容易產生破裂的課題。又,專利文獻3所記載之構件,係藉由令板厚之表層部為軟質組織,並令板厚之中央部為硬質組織與軟質組織的複合組織,來減低板厚方向上急遽之硬度梯度。然而,由於是令板厚之中央部為複合組織,因此拉伸強度的上限會成為1300MPa左右,而要確保對於熱壓製零件所要求之拉伸強度1500MPa以上是很困難的。
先前技術文獻 專利文獻 專利文獻1:日本專利特開2015-30890號公報 專利文獻2:日本專利特開2006-104546號公報 專利文獻3:國際專利公開第2015/097882號
發明概要 發明欲解決之課題 本發明有鑑於習知技術之課題,目的在於提供一種耐撞擊特性及耐氫脆化特性優異之熱壓印成形體。
用以解決課題之手段 本發明人等針對解決上述課題之方法進行了精闢研討。首先,要提升耐氫脆化特性,是以減低板厚表層之晶格缺陷密度為有效,為此,必須在表層形成軟質組織。另一方面,為了確保1500MPa以上之拉伸強度,必須僅以硬質組織構成板厚之中央部。於是,本發明人等想到當令板厚之表層為軟質組織,並以硬質組織構成板厚之中央部時,只要可以減低在硬質組織與軟質組織之邊界附近產生之板厚方向之急遽的硬度梯度,便可確保1500MPa以上的拉伸強度與良好之耐氫脆化特性,並獲得良好彎曲性。具體而言,係在硬質組織與軟質組織之邊界形成具有該等組織之中間硬度的組織(中間層),藉此來減低板厚方向之硬度梯度,以緩和彎曲變形時之應力集中。其結果,便可抑制彎曲變形時產生破裂,而可確保1500MPa以上之拉伸強度與良好之耐氫脆化特性,並可獲得良好彎曲性,而能獲得耐撞擊特性與耐氫脆化特性優異之熱壓印成形體。
又,本發明人等發現到藉由將板厚之中央部的Mn添加量控制為較高的值,更具體地來說是控制在1.50%以上且小於3.00%,便可提高淬火性以縮小成形體中之硬度參差,亦即可以穩定確保高強度。就其結果而言,可以確保1500MPa以上之拉伸強度與良好的耐氫脆化特性,而不僅由彎曲性的觀點且由強度穩定性(硬度參差)的觀點來看也可以獲得耐撞擊特性優異之熱壓印成形體。
而且,本發明人等發現到藉由將板厚之中央部的Si添加量控制為較高的值,更具體地來說是控制在大於0.50%且小於3.00%以確保有助於提升變形能力的組織,而可藉此提高延展性。就其結果而言,可以確保1500MPa以上之拉伸強度與良好的耐氫脆化特性,而不僅由彎曲性的觀點且由延展性的觀點來看也可以獲得耐撞擊特性優異之熱壓印成形體。
此外,本發明人等發現到藉由將板厚之中央部的Mn及Si添加量控制為較高的值,更具體地來說是分別控制在1.50%以上且小於3.00%以及大於0.50%且小於3.00%,便可提升延展性,並且提高淬火性以縮小成形體中之硬度參差,亦即可以穩定確保高強度。就其結果而言,可以確保1500MPa以上之拉伸強度與良好的耐氫脆化特性,而不僅由彎曲性的觀點且由強度穩定性(硬度參差)及延展性的觀點來看也可以獲得耐撞擊特性優異之熱壓印成形體。
本發明是根據上述見解而完成者,其要旨如下。 (1)一種熱壓印成形體,包含板厚中央部與配置於該板厚中央部的兩側或單側之表層, 該熱壓印成形體之特徵在於:前述熱壓印成形體更包含中間層,該中間層係形成於前述板厚中央部與各表層之間且與該等相鄰接;前述板厚中央部以質量%計含有:C:0.20%以上且小於0.70%、Si:小於3.00%、Mn:0.20%以上且小於3.00%、P:0.10%以下、S:0.10%以下、sol.Al:0.0002%以上且在3.0000%以下、N:0.01%以下,且剩餘部分由Fe及無法避免之不純物所構成;前述板厚中央部之硬度為500Hv以上且800Hv以下;前述表層之板厚方向的硬度變化ΔH1
為10Hv以上且小於200Hv;前述中間層之板厚方向的硬度變化ΔH2
為50Hv以上且小於200Hv。 (2)如上述(1)之熱壓印成形體,其中前述板厚中央部之Si含量為0.50%以下,且前述板厚中央部之Mn含量為0.20%以上且小於1.50%。 (3)如上述(1)之熱壓印成形體,其中前述板厚中央部之Si含量為0.50%以下,且前述板厚中央部之Mn含量為1.50%以上且小於3.00%。 (4)如上述(1)之熱壓印成形體,其中前述板厚中央部之Si含量為大於0.50%且小於3.00%,前述板厚中央部之Mn含量為0.20%以上且小於1.50%,並且前述板厚中央部以面積分率計包含1.0%以上且小於5.0%的殘留沃斯田鐵。 (5)如上述(1)之熱壓印成形體,其中前述板厚中央部之Si含量為大於0.50%且小於3.00%,前述板厚中央部之Mn含量為1.50%以上且小於3.00%,並且前述板厚中央部以面積分率計包含1.0%以上且小於5.0%的殘留沃斯田鐵。 (6)如上述(1)至(5)中任一項之熱壓印成形體,其中前述板厚中央部以質量%計更含有Ni:0.01%以上且在3.00%以下。 (7)如上述(1)至(6)中任一項之熱壓印成形體,其中前述板厚中央部以質量%計更含有下述1種或2種以上元素: Nb:0.010%以上且在0.150%以下、Ti:0.010%以上且在0.150%以下、Mo:0.005%以上且在1.000%以下及B:0.0005%以上且在0.0100%以下。 (8)如上述(1)至(7)中任一項之熱壓印成形體,其於各表層之表面更包含鍍敷層。
發明效果 根據本發明,便可實現優異彎曲性,並可提供一種耐撞擊特性與耐氫脆化特性優異的熱壓印成形體。又,根據本發明,將板厚之中央部的Mn添加量控制為較高的值,藉此不僅由彎曲性的觀點且由強度穩定性(硬度參差)的觀點來看也可以更加改善耐撞擊特性。而且,根據本發明,將板厚之中央部的Si添加量控制為較高的值,藉此不僅由彎曲性的觀點且由延展性的觀點來看也可以更加改善耐撞擊特性。此外,根據本發明,將板厚之中央部的Mn及Si添加量控制為較高的值,藉此不僅由彎曲性的觀點且由強度穩定性(硬度參差)及延展性的觀點來看也可以更加改善耐撞擊特性。
發明實施形態 以下,說明本發明之熱壓印成形體與其製造方法。
首先,說明構成本發明之熱壓印成形體之板厚中央部之成分組成的限定理由。以下,關於成分組成之符號%意指質量%。
「C:0.20%以上且小於0.70%」 C係用以在板厚中央部獲得500Hv以上且800Hv以下之硬度的重要元素。若小於0.20%,將難以在板厚中央部確保500Hv以上,因此C是設為0.20%以上。且較佳是在0.30%以上。另一方面,若為0.70%以上,則板厚中央部之硬度會大於800Hv而導致彎曲性降低,因此C是設為小於0.70%。且較佳是在0.50%以下。
「Si:小於3.00%」 由於Si係可藉由固溶強化而有助於提升強度的元素,因此由提升強度的觀點來看亦可將上限設為0.50%而作添加。另一方面,即使添加大於0.50%,提升強度的效果仍會飽和,因此將上限設為0.50%。且較佳是在0.30%以下。並且,Si亦為具有可在不損及藉由控制表層組織而展現之耐氫脆化特性及彎曲性的前提下提高延展性之效果的元素。尤其是,若汽車撞擊時產生彎曲變形,會因帽形構件翹曲而使變形局部化,導致作為構件之耐荷重降低。亦即,構件與最大荷重不僅會受到構件強度的影響,還會受到容易產生翹曲的程度影響。若構件狀態中鋼板之延展性高,變形區域便會變得不易局部化。亦即不易翹曲。因此在熱壓印構件中延展性也很重要,但一般來說麻田散鐵的延展性低。由上述觀點來看,藉由添加大於0.50%之Si,便可確保以面積分率計1.0%以上之殘留沃斯田鐵而提升延展性,因此Si是以添加大於0.50%為佳。且較佳是在1.00%以上。另一方面,當添加3.00%以上,殘留沃斯田鐵以面積分率計會成為5.0%以上,而會招致彎曲性之劣化,因此將上限設為小於3.00%。且較佳是小於2.00%。
「Mn:0.20%以上且小於3.00%」 Mn係可藉由固溶強化而有助於提升強度的元素。由提升強度的觀點來看,若小於0.20%將無法獲得效果,因此要添加0.20%以上。且較佳是在0.70%以上。另一方面,即使添加1.50%以上,提升強度之效果仍會飽和,因此以小於1.50%為上限。並且,Mn亦為具有可在不損及藉由控制表層組織而展現之耐氫脆化特性及彎曲性的前提下提高淬火性之效果的元素。在熱壓印成形體中,接觸模具的方式並不一定相同,例如在帽形構件之縱壁部等中冷卻速度容易降低。因此於鋼板上會有局部性地形成硬度較低之區域的情況。局部性之軟化部於撞擊時變形會集中,而成為發生破裂的主要原因,因此提高淬火性並縮小成形體中的硬度參差,亦即確保穩定之強度,在確保耐撞擊特性上是很重要的。由上述觀點來看,藉由添加1.50%以上之Mn,便可提高淬火性並穩定獲得高強度,因此Mn是以添加1.50%以上為佳。且較佳是在1.70%以上。另一方面,即使添加3.00%以上,強度穩定性之效果仍會飽和,因此其上限是設為小於3.00%。且較佳是小於2.00%。
「P:0.10%以下」 P係會偏析於晶界而阻礙晶界強度的元素。當大於0.10%時,晶界強度會明顯降低,且耐氫脆化特性及彎曲性會降低,因此P是設為0.10%以下。且較佳是在0.05%以下。下限雖無特別限定,但若減低至小於0.0001%,脫P成本便會大幅上升,於經濟面相當不利,故在實用鋼板上0.0001%為實質下限。
「S:0.10%以下」 S係會形成夾雜物的元素。當大於0.10%時,會生成夾雜物且耐氫脆化特性及彎曲性降低,因此S是設為0.10%以下。且較佳是在0.005%以下。下限雖無特別限定,但若減低至小於0.0015%,脫S成本便會大幅上升,於經濟面相當不利,故在實用鋼板上0.0015%為實質下限。
「sol.Al:0.0002%以上且在3.0000%以下」 Al係可發揮將熔鋼脫氧而使鋼健全化之作用的元素。若小於0.0002%,脫氧會不充分,因此sol.Al是設為0.0002%以上。且較佳是在0.0010%以上。另一方面,即使添加大於3.0000%,該效果仍會飽和,因此將其設為3.0000%以下。
「N:0.01%以下」 N係不純物元素,且係形成氮化物而阻礙彎曲性之元素。當大於0.01%時,會生成粗大氮化物而導致彎曲性明顯降低,因此N是設為0.01%以下。且較佳是在0.0075%以下。下限雖無特別限定,但若減低至小於0.0001%,脫N成本便會大幅上升,於經濟面相當不利,故在實用鋼板上0.0001%為實質下限。
「Ni:0.01%以上且在3.00%以下」 Ni係可藉由固溶強化而有助於提升強度的元素,因此亦可視需要來添加。若小於0.01%將無法獲得效果,故要添加0.01%以上。且較佳是在0.50%以上。另一方面,即使添加大於3.00%,該效果仍會飽和,因此將其設為3.00%以下。且較佳是在2.50%以下。
「Nb:0.010%以上且在0.150%以下」 Nb係可藉由固溶強化而有助於提升強度的元素,因此亦可視需要來添加。若小於0.010%將無法獲得效果,故要添加0.010%以上。且較佳是在0.035%以上。另一方面,即使添加大於0.150%,該效果仍會飽和,因此將其設為0.150%以下。且較佳是在0.120%以下。
「Ti:0.010%以上且在0.150%以下」 Ti係可藉由固溶強化而有助於提升強度的元素,因此亦可視需要來添加。若小於0.010%將無法獲得效果,故要設為0.010%以上。且較佳為0.020%。另一方面,即使添加大於0.150%,該效果仍會飽和,因此將其設為0.150%以下。且較佳是在0.120%以下。
「Mo:0.005%以上且在1.000%以下」 Mo係可藉由固溶強化而有助於提升強度的元素,因此亦可視需要來添加。若小於0.005%將無法獲得效果,故要設為0.005%以上。且較佳是在0.010%以上。另一方面,即使添加大於1.000%,該效果仍會飽和,因此將其設為1.000%以下。且較佳是在0.800%以下。
「B:0.0005%以上且0.0100%以下」
B係會偏析於晶界而有助於提升晶界強度的元素,因此亦可視需要來添加。若小於0.0005%將無法充分獲得添加效果,故要添加0.0005%以上。且較佳是在0.0010%以上。另一方面,即使添加大於0.0100%,該效果仍會飽和,因此將其設為0.0100%以下。且較佳是在0.0075%以下。
板厚中央部之成分組成的剩餘部分為Fe及無法避免之不純物。無法避免之不純物係從鋼原料及/或製鋼過程中無法避免地混入,並在不阻礙本發明之熱壓印成形體之特性的範圍內所容許的元素。
其次,說明構成本發明之熱壓印成形體的表層之成分組成。
針對表層之成分,是以C含量、Si含量及Mn含量中任1種或2種以上為板厚中央部之對應元素含量的0.6倍以下為佳,且該情況下之各個成分的較佳範圍如下。
「C:0.05%以上且小於0.42%」
C係為了提高強度而添加。若小於0.05%將無法獲得效果,故要添加0.05%以上。而在提高作為構件之耐荷重以提升衝擊特性的觀點上,係以0.10%以上為宜。另一方面,為了使表層的硬度比板厚中央部的硬度低,宜令其較板厚中央部少。因此,表層之較佳C含量為小於0.42%,且宜在0.35%以下。
「Si:小於2.00%」 Si係可藉由固溶強化而有助於提升強度的元素,因此會為了提高強度而添加。惟,為了使表層的硬度比板厚中央部的硬度低,宜令其較板厚中央部少。因此,表層之較佳Si含量為小於2.00%,且宜在1.50%以下,較宜為0.30%以下,更宜為0.20%以下。
「Mn:0.01%以上且小於1.80%」 Mn係可藉由固溶強化而有助於提升強度的元素,因此會為了提高強度而添加。惟,為了使表層的硬度比板厚中央部的硬度低,宜令其較板厚中央部少。因此,表層之較佳Mn含量為小於1.80%,且宜在1.40%以下,較宜為小於0.90%,更宜為0.70%以下。
針對表層之其他成分並無特別限定。一般來說,除了C、Si及Mn以外,表層亦可任意選擇而含有下述成分中之1種或2種以上成分。
「P:0.10%以下」 P係會偏析於晶界而阻礙晶界強度的元素。當大於0.10%時,晶界強度會明顯降低,且耐氫脆化特性及彎曲性會降低,因此P是設為0.10%以下。且較佳是在0.05%以下。下限雖無特別限定,但若減低至小於0.0001%,脫P成本便會大幅上升,於經濟面相當不利,故在實用鋼板上0.0001%為實質下限。
「S:0.10%以下」 S係會形成夾雜物的元素。當大於0.10%時,會生成夾雜物且耐氫脆化特性及彎曲性降低,因此S是設為0.10%以下。且較佳是在0.005%以下。下限雖無特別限定,但若減低至小於0.0015%,脫S成本便會大幅上升,於經濟面相當不利,故在實用鋼板上0.0015%為實質下限。
「sol.Al:0.0002%以上且在3.0000%以下」 Al係可發揮將熔鋼脫氧而使鋼健全化之作用的元素。若小於0.0002%,脫氧會不充分,因此sol.Al是設為0.0002%以上。且較佳是在0.0010%以上。另一方面,即使添加大於3.0000%,該效果仍會飽和,因此將其設為3.0000%以下。
「N:0.01%以下」 N係不純物元素,且係形成氮化物而阻礙彎曲性之元素。當大於0.01%時,會生成粗大氮化物而導致彎曲性明顯降低,因此N是設為0.01%以下。且較佳是在0.0075%以下。下限雖無特別限定,但若減低至小於0.0001%,脫N成本便會大幅上升,於經濟面相當不利,故在實用鋼板上0.0001%為實質下限。
「Ni:0.01%以上且在3.00%以下」 Ni係可藉由固溶強化而有助於提升強度的元素,因此亦可視需要來添加。若小於0.01%將無法獲得效果,故要添加0.01%以上。且較佳是在0.50%以上。另一方面,即使添加大於3.00%,該效果仍會飽和,因此將其設為3.00%以下。且較佳是在2.50%以下。
「Nb:0.010%以上且在0.150%以下」 Nb係可藉由固溶強化而有助於提升強度的元素,因此亦可視需要來添加。若小於0.010%將無法獲得效果,故要添加0.010%以上。且較佳是在0.035%以上。另一方面,即使添加大於0.150%,該效果仍會飽和,因此將其設為0.150%以下。且較佳是在0.120%以下。
「Ti:0.010%以上且在0.150%以下」 Ti係可藉由固溶強化而有助於提升強度的元素,因此亦可視需要來添加。若小於0.010%將無法獲得效果,故要設為0.010%以上。且較佳為0.020%。另一方面,即使添加大於0.150%,該效果仍會飽和,因此將其設為0.150%以下。且較佳是在0.120%以下。
「Mo:0.005%以上且在1.000%以下」 Mo係可藉由固溶強化而有助於提升強度的元素,因此亦可視需要來添加。若小於0.005%將無法獲得效果,故要設為0.005%以上。且較佳是在0.010%以上。另一方面,即使添加大於1.000%,該效果仍會飽和,因此將其設為1.000%以下。且較佳是在0.800%以下。
「B:0.0005%以上且0.0100%以下」 B係會偏析於晶界而有助於提升晶界強度的元素,因此亦可視需要來添加。若小於0.0005%將無法充分獲得添加效果,故要添加0.0005%以上。且較佳是在0.0010%以上。另一方面,即使添加大於0.0100%,該效果仍會飽和,因此將其設為0.0100%以下。且較佳是在0.0075%以下。
表層之成分組成的剩餘部分為Fe及無法避免之不純物。無法避免之不純物係從鋼原料及/或製鋼過程中無法避免地混入,並在不阻礙本發明之熱壓印成形體之特性的範圍內所容許的元素。
接著,說明本發明之熱壓印成形體的微觀組織。
「板厚中央部之硬度為500Hv以上且800Hv以下」 當板厚中央部之硬度在500Hv以上時,可以確保熱壓印成形體之拉伸強度為1500MPa以上。且較佳是在600Hv以上。另一方面,當板厚中央部之硬度大於800Hv時,與表層及中間層之硬度差會變得過大而招致彎曲性的劣化,因此將800Hv設為上限。且較佳是在720Hv以下。
「板厚中央部以面積分率計包含1.0%以上且小於5.0%之殘留沃斯田鐵」 將板厚中央部中之Si含量控制為大於0.50%且小於3.00%,且令該板厚中央部以面積分率計包含1.0%以上且小於5.0%之殘留沃斯田鐵作為金屬組織,藉此便可提升所獲得之熱壓印成形體的延展性。且較佳是在2.0%以上。另一方面,當殘留沃斯田鐵的面積分率成為5.0%以上時,會招致彎曲性的劣化,故要將上限設為小於5.0%。且較佳是小於4.5%。
本發明中,殘留沃斯田鐵的面積分率可用以下方法測定。由熱壓印成形後之構件採取試料後,由軋延面法線方向起表面切削至板厚之1/4深度為止,並供予X射線繞射測定。可從藉由使用有Mo之Kα線的X射線繞射法而得之影像,利用下式來決定殘留沃斯田鐵的面積分率Vγ。
Vγ=(2/3){100/(0.7×α(211)/γ(220)+1)}+(1/3){100/(0.78×α(211)/γ(311)+1)}
此處,α(211)係肥粒鐵之(211)面的反射面強度,γ(220)係沃斯田鐵之(220)面的反射面強度,γ(311)係沃斯田鐵之(311)面的反射面強度。
「表層之板厚方向的硬度變化△H1為10Hv以上且小於200Hv,中間層之板厚方向的硬度變化△H2為50Hv以上且小於200Hv」
本發明中,所謂表層意指從熱壓印成形體之兩面或單面起到該熱壓印成形體之板厚的8%為止的區域,亦即各表層具有熱壓印成形體之板厚8%的厚度。同樣地,本發明中,所謂中間層意指從熱壓印成形體之兩面或單面起到該熱壓印成形體之板厚的20%為止的區域當中除去上述表層的部分,亦即各中間層具有熱壓印成形體之板厚12%的厚度。又,本發明中,所謂板厚中央部意指由熱壓印成形體除去上述表層及中間層後所得的部分,亦即若為在該板厚中央部之兩側配置有表層及中間層的熱壓印成形體時,板厚中央部具有該熱壓印成形體之板厚60%的厚度,而若為僅於該板厚中央部之單側配置有表層及中間層的熱壓印成形體時,板厚中央部則具有該熱壓印成形體之板厚80%的厚度。此處,△H1係顯示表層之板厚方向的硬度變化,而△H2則顯示中間層之板厚方向的硬度變化。本發明人等進行精闢討論之結果,發現由彎曲性等效果的觀點來看,該區域之硬度變化(ΔH1
、ΔH2
)是很重要的,當ΔH1
為10Hv以上且小於200Hv時,可獲得良好之彎曲性及耐氫脆性。由於具有上述之良好彎曲性,故可以緩和撞擊時之彎曲變形等所造成的應力而抑制破裂及龜裂,因此在熱壓印成形體中可達成優異耐撞擊特性。另一方面,當ΔH1
小於10Hv時,將無法獲得此種緩和彎曲變形時之應力的效果,且龜裂變得容易從表層進展,因此將下限設為10Hv。且較佳是在20Hv以上,更佳是在30Hv以上。又,當ΔH1
小於200Hv時,緩和彎曲變形時之應力集中的效果被提高而可獲得良好彎曲性,因此將上限設為小於200Hv。且較佳為小於150Hv,更佳為小於100Hv或在95Hv以下,最佳是在90Hv以下。
同樣地,可知當ΔH2
為50Hv以上且小於200Hv時,能夠獲得良好彎曲性。若ΔH2
為200Hv以上,由於中間層之硬度梯度變得急遽,會變得難以緩和彎曲變形時之應力集中,而彎曲性劣化,因此將上限設為小於200Hv。且較佳是在190Hv以下,更佳是在180Hv以下。又,下限以60Hv以上為佳,在70Hv以上更佳。
板厚中央部之硬度的測定方法如以下。採取與熱壓印成形體之板面呈垂直之截面後,進行測定面之試料的調製,並供予硬度試驗。測定面之調製方法只要依據JIS Z 2244來實施即可,例如使用#600到#1500之碳化矽紙研磨測定面後,使用令粒度1μm到6μm之鑽石粉末在酒精等稀釋液或純水中分散而得之液體來加工成鏡面即可。而硬度試驗只要是以JIS Z 2244所記載之方法來實施即可,使用微維氏硬度試驗機於熱壓印成形體之板厚1/2位置上,以荷重1kgf且以壓痕之3倍以上的間隔測定10點,並以其平均值作為板厚中央部的硬度。
接著,說明表層及中間層之硬度的測定方法。採取與熱壓印成形體之板面呈垂直之截面後,進行測定面之試料的調製,並供予硬度試驗。為了正確測定熱壓印成形體之表面附近的硬度,測定面之調製係以極力縮小凹凸且在表面附近不產生塌凹的方式來實施。例如,使用日本電子製的截面拋光機(Cross section polisher)以氬離子束濺鍍測定面。此時,在抑制測定面上產生條紋狀凹凸之目的下,亦可使用日本電子製之試料旋轉保持具,由360度方向對測定面照射氬離子束。
當是在板厚中央部之兩側配置有表層及中間層的熱壓印成形體時,使用微維氏硬度試驗機對已調製測定面之試料實施2次測定。第1次係於從熱壓印成形體之第1表面起到該熱壓印成形體之板厚的20%為止之區域中,在與板面成直角的方向(板厚方向)上以荷重1kgf且以壓痕之3倍以上的間隔進行測定。此時,雖然測定點之合計會因熱壓印成形體之板厚而不同,但為了算出後述之ΔH1
及ΔH2
,只要進行至少2點以上之測定即可。熱壓印成形體之最表面側的測定位置,係設定於從板面(當有鍍敷層存在時,為鍍敷層之正下或鍍敷層與母材之間的合金層的正下)起到20μm以內為止之區域中進行。第2次的測定係從與第1次為相反側之熱壓印成形體的表面實施。亦即,於從熱壓印成形體之第2表面起到板厚之20%為止之區域中,在與板面成垂直的方向(板厚方向)上以荷重1kgf且以壓痕之3倍以上的間隔進行測定。熱壓印成形體之最表面側的測定位置,係設定於從板面(當有鍍敷層存在時,為鍍敷層之正下或鍍敷層與母材之間的合金層的正下)起到20μm以內為止之區域中進行。
當是僅於板厚中央部之單側配置有表層及中間層的熱壓印成形體時,使用微維氏硬度試驗機對已調製測定面之試料,於從熱壓印成形體之表層起到該熱壓印成形體之板厚的20%為止之區域中,在與板面成直角的方向(板厚方向)上以荷重1kgf且以壓痕之3倍以上的間隔進行測定。此時,雖然測定點之合計會因熱壓印成形體之板厚而不同,但為了算出後述之ΔH1
及ΔH2
,只要進行至少2點以上之測定即可。熱壓印成形體之最表面側的測定位置,係設定於從板面(當有鍍敷層存在時,為鍍敷層之正下或鍍敷層與母材之間的合金層的正下)起到20μm以內為止之區域中進行。
接下來,針對當是於板厚中央部之兩側配置有表層及中間層的熱壓印成形體時的ΔH1
計算方法進行說明。首先,由從熱壓印成形體之第1表面起到板厚8%為止之區域中所包含的所有測定點,以式(1)算出第1表面側表層之硬度梯度Δa。此處,ai
係第i個測定點距離第1表面的距離(μm),ci
係ai
之維氏硬度(Hv),n係從第1表面起到板厚8%為止之區域中所包含的所有測定點之合計。接著,利用從熱壓印成形體之第2表面起到板厚8%為止之區域中所包含的所有測定點,以式(2)算出第2表面側表層之硬度梯度Δb。此處,bi
係第i個測定點距離第2表面的距離(μm),di
係bi
之維氏硬度(Hv),m係從第2表面起到板厚8%為止之區域中所包含的所有測定點之合計。在算出Δa及Δb之後,利用式(3-1)算出表層之板厚方向的硬度變化ΔH1
。此處,t為熱壓印成形體之板厚(μm)。
另一方面,當是僅於板厚中央部之單側配置有表層及中間層的熱壓印成形體時,利用式(3-2)算出表層之板厚方向的硬度變化ΔH1
。
接下來,針對當是於板厚中央部之兩側配置有表層及中間層的熱壓印成形體時的ΔH2
計算方法進行說明。首先,由從熱壓印成形體之第1表面側之板厚8%的位置起到板厚20%為止之區域中所包含的所有測定點,以式(4)算出第1表面側中間層之硬度梯度ΔA。此處,Ai
係第i個測定點距離第1表面的距離(μm),Ci
係Ai
之維氏硬度(Hv),N係第1表面側之從板厚8%的位置起到板厚20%為止之區域中所包含的所有測定點之合計。接著,由從熱壓印成形體之第2表面側之板厚8%的位置起到板厚20%為止之區域中所包含的所有測定點,以式(5)算出第2表面側中間層之硬度梯度ΔB。此處,Bi
係第i個測定點距離第2表面的距離(μm),Di
係Bi
之維氏硬度(Hv),M係第2表面側之從板厚的8%起到20%為止的區域中所包含的所有測定點之合計。在算出ΔA及ΔB之後,利用式(6-1)算出中間層之板厚方向的硬度變化ΔH2
。
另一方面,當是僅於板厚中央部之單側配置有表層及中間層的熱壓印成形體時,利用式(6-2)算出表層之板厚方向的硬度變化ΔH2
。
[數學式1]此處, ΔH1
:表層之板厚方向的硬度變化(Hv) Δa:第1表面側表層之硬度梯度(Hv/μm) ai
:第i個測定點距離第1表面的距離(μm) ci
:ai
之維氏硬度(Hv) n:第1表面側表層所包含之所有測定點的合計 Δb:第2表面側表層之硬度梯度(Hv/μm) bi
:第i個測定點距離第2表面的距離(μm) di
:bi
之維氏硬度(Hv) m:第2表面側表層所包含之所有測定點的合計 ΔH2
:中間層之板厚方向的硬度變化(Hv) ΔA:第1表面側中間層之硬度梯度(Hv/μm) Ai
:第i個測定點距離第1表面的距離(μm) Ci
:Ai
之維氏硬度(Hv) N:第1表面側中間層所包含之所有測定點的合計 ΔB:第2表面側中間層之硬度梯度(Hv/μm) Bi
:第i個測定點距離第2表面的距離(μm) Di
:Bi
之維氏硬度(Hv) M:第2表面側中間層所包含之所有測定點的合計 t:板厚(μm)。
就提升耐蝕性等目的而言,在熱壓印成形體之各表層之表面上亦可形成鍍敷層。鍍敷層為電鍍層及熔融鍍敷層之任一者皆可。電鍍層包含例如:電鍍鋅層、電鍍Zn-Ni合金層等。
熔融鍍敷層包含例如:熔融鍍鋅層、合金化熔融鍍鋅層、熔融鍍鋁層、熔融Zn-Al合金鍍層、熔融Zn-Al-Mg合金鍍層、熔融Zn-Al-Mg-Si合金鍍層等。鍍敷層之附著量並無特別限制,為一般的附著量即可。
接著,說明用以製得本發明之熱壓印成形體之製法的形態。以下之說明,僅意欲例示用以製得本發明之熱壓印成形體之製法,而非意欲將本發明之熱壓印成形體限定為如以下說明之由積層2片鋼板而成之多層鋼板製得者。例如,也可以將單層鋼板作脫碳處理以軟化其表層部分,而藉此製得由表層與板厚中央部所構成之高強度鋼板,並與多層鋼板之情況同樣地將其進行熱處理等來製造。
熔製滿足上述板厚中央部之成分的母材鋼板並磨削兩面或單面而除去表面氧化物後,以電弧熔接將表層用鋼板接著於該兩面或單面上。此外,以積層C含量、Si含量及Mn含量中任1個或2個以上為母材鋼板之對應元素含量的0.6倍以下之表層用鋼板為佳。雖然理由尚不明確,但調查顯示出優異彎曲性之熱壓印成形體的結果,係為表層用鋼板之C含量、Si含量及Mn含量中任1個或2個以上為母材鋼板之對應元素含量的0.6倍以下。
藉由對上述積層體(多層鋼板)施行熱軋延、冷軋延、熱壓印、連續熔融鍍敷等,便可製得本發明之高強度鋼板,更具體地來說係可製得熱壓印成形體。
例如,當要製得熱軋鋼板時,宜將以上述方法製作而得之多層鋼板在1100℃以上且1350℃以下的溫度下維持20分鐘以上且小於60分鐘。藉由施行上述熱處理,便可將熱壓製後之表層中板厚方向之硬度變化ΔH1
控制為10Hv以上且小於200Hv,特別是可控制為小於100Hv。又,藉由上述熱處理,可以在母材鋼板與表層用鋼板之間使元素擴散而在兩者之間形成中間層,進而可將熱壓製後之該中間層中板厚方向的硬度變化ΔH2
控制為50Hv以上且小於200Hv。對照之下,若加熱溫度小於1100℃,熱壓製後之表層中板厚方向的硬度變化ΔH1
會大於200Hv,且熱壓製後之中間層中板厚方向的硬度變化ΔH2
會小於10Hv。在這種情況下,會助長氫從熱壓印成形體表面入侵,而招致耐氫脆化特性的劣化,進而無法獲得良好彎曲性,故將下限設為1100℃。另一方面,當加熱溫度大於1350℃時,ΔH1
會變成小於10Hv,而且ΔH2
會大於200Hv,而無法獲得良好彎曲性,故將上限設為1350℃。而加熱維持宜進行20分鐘以上且小於60分鐘。本發明人等進行精闢討論後之結果,發現當維持時間為20分鐘以上且小於60分鐘時,可獲得良好耐氫脆性及彎曲性,且此時所獲得之微觀組織之ΔH2
會在50Hv以上且小於200Hv。故,將維持時間設為20分鐘以上且小於60分鐘。
又,為了更加促進本發明之中間層的形成,多層鋼板之上述熱處理後的熱軋延宜包含粗軋延及完工軋延,且該粗軋延宜於粗軋延溫度為1100℃以上、每1道次之板厚減少率為5%以上且小於50%及道次間時間為3秒以上的條件下實施2次以上。
具體而言,為了更加促進本發明之中間層的形成,必須要控制合金元素,尤其要控制C原子的濃度以使其平緩地分布。C濃度之分布可藉由C原子的擴散而得,且越高溫C原子之擴散頻率就越增加。因此,為了控制C濃度,由熱軋加熱到粗軋延中之控制就變得很重要。熱軋加熱中,為了促進C原子之擴散,必須將加熱溫度高溫化,較佳為1100℃以上且在1350℃以下,更佳為高於1150℃且在1350℃以下。熱軋加熱中會產生圖(1)所示之(i)及(ii)的變化。(i)係從板厚中央部往表層之C原子的擴散,(ii)係從表層往外部脫離之C的脫碳反應。且依該(i)與(ii)之C原子的擴散及脫離反應的平衡而會在C濃度上產生分布。若小於1100℃,由於(i)之反應不足,故無法獲得較佳之C濃度分布。另一方面,若高於1350℃,由於(ii)之反應會過度產生,故同樣無法獲得較佳之濃度分布。
在藉由調節熱軋加熱溫度而控制為較佳的C濃度分布後,為了更進一步獲得最佳C濃度分布,粗軋延中之道次控制就變得極為重要。粗軋延係於粗軋延溫度為1100℃以上、每1道次之板厚減少率為5%以上且小於50%以及道次間時間為3秒以上的條件下實施2次以上。這是由於藉由粗軋延所導入之應變,可促進圖(1)中(i)之C原子的擴散。假如以常規方法將以熱軋加熱而將C濃度控制於較佳狀態後的鋼胚進行粗軋延及完工軋延,板厚便會在C原子無法於表層內充分擴散的狀態下減少。因此,若以常規方法的熱軋來從具有大於200mm之厚度的鋼胚製造數mm之厚度的熱軋鋼板,便會成為在表層中C濃度急遽變化的鋼板,而變得無法獲得平緩之硬度變化。為了解決此情況而發現的方法即是上述之粗軋延的道次控制。C原子之擴散,不僅會受溫度影響,還會受到應變(差排密度)的影響甚大。尤其是相較於晶格擴散,差排擴散的擴散頻率會提高為10倍以上,因此需要下工夫來留下差排密度,並藉由軋延令板厚變薄。圖2之曲線1係顯示在粗軋延之每1道次的板厚減少率小之情況下軋延道次後之差排密度變化,並可知應變持續長時間殘存。藉由如上所述地使應變持續長時間殘存於表層中,表層內之C原子的擴散便會充分產生,而可獲得最佳C濃度分布。另一方面,曲線2係在板厚減少率大的情況下差排密度的變化,當軋延所導入之應變量升高時,會變得容易促進恢復,而使差排密度急遽降低。因此,為了獲得最佳C濃度分布,必須令如曲線2之差排密度的變化不會產生。由上述觀點來看,每1道次之板厚減少率上限會是小於50%。此外,為了促進C原子在表層的擴散,必須確保一定量之差排密度與維持時間,因此板厚減少率之下限會是5%,且作為道次間時間必須確保在3秒以上。
完工軋延係以一般條件實施之完工軋延即可。例如,只要在完工溫度亦為810℃以上的溫度區中實施即可,且亦不須特別規定其後接續之冷卻條件,而在750℃以下之溫度區中實施捲取。又,亦可實施以熱軋鋼板的軟質化為目的之再加熱處理。
熱壓印時之加熱、成型及冷卻步驟亦以一般條件實施即可。例如,對於將熱軋延步驟中所捲取之熱軋鋼板捲回後的熱軋鋼板、或經捲取之熱軋鋼板捲回並施行冷軋延後的冷軋鋼板、或者冷軋鋼板施行鍍敷,並以0.1℃/s以上且200℃/s以下的加熱速度加熱至810℃以上且在1000℃以下之溫度,並以一般之熱壓印將已維持於該溫度的鋼板成形為預定形狀。維持時間只要依成形態樣設定即可,故並無特別限定,但要將有30秒以上且600秒以下即可之熱壓印後的成形體冷卻至室溫。冷卻速度亦設定為一般條件即可,例如,由加熱溫度到400℃為止之溫度區中的平均冷卻速度只要在50℃/s以上即可。若係板厚中央部之Si含量為大於0.50%且小於3.00%,且板厚中央部之Mn含量為0.20%以上且小於1.50%的鋼鈑、以及板厚中央部之Si含量為大於0.50%且小於3.00%,且板厚中央部之Mn含量為1.50%以上且小於3.00%的鋼鈑時,以使殘留沃斯田鐵之生成量增加並提升延展性為目的,在加熱維持後之冷卻中,宜將200℃以上且400℃以下之溫度區中的平均冷卻速度控制為小於50℃/s。此外,以調整強度等為目的,亦可在150℃~600℃之範圍內對已冷卻至室溫的成形體施行回火處理。
冷軋延為以一般之軋縮率例如30~90%進行之冷軋延即可。熱軋鋼板及冷軋鋼板,除維持熱軋延及冷軋延後之狀態者以外,亦包含以一般條件對熱軋鋼板或冷軋鋼板施行過再結晶退火的鋼板、及經以一般條件施行調質軋延的鋼板。且鍍敷條件並無特別限定,一般條件即可。並視需要,以一般鍍敷條件於熱軋鋼板、冷軋鋼板、或對冷軋鋼板施行再結晶退火及/或調質軋延而得的鋼板上施行鍍敷。
實施例 接下來,說明本發明實施例,惟,實施例中之條件僅為用以確認本發明之可實施性及效果所採用的一條件例,且本發明不受該一條件例限定。只要能在不脫離本發明之宗旨下達成本發明之目的,本發明可採用各種條件。
於本實施例中,利用先前敘述之方法測定熱壓印後之鋼板的硬度,並算出板厚中央部之硬度、表層之板厚方向的硬度變化ΔH1
及中間層之板厚方向的硬度變化ΔH2
。
並且,實施了熱壓印後之鋼板的拉伸試驗。拉伸試驗係製作JIS Z 2201所記載之5號試驗片,並依照JIS Z 2241所記載之試驗方法實施。
熱壓印成形體之耐氫脆化特性係使用由成形體切出之試驗片進行評估。一般而言,熱壓印成形體係使用點熔接等接合手法來與其他零件接合,並依零件形狀精度對熱壓印成形體施加扭轉以附加應力。應力會隨著零件之位置而異,而難以將其正確算出,但認為只要不因降伏應力而產生延遲破壞,在實用上就沒有問題。因此,由成形體切出板厚1.2mm×寬6mm×長68mm的試驗片,並利用四點彎曲試驗賦予相當於降伏應力的應變後浸漬於pH3之鹽酸中100h,再以有無產生破裂來評估耐氫脆化特性。令無斷裂時為合格(○),且令有斷裂時為不合格(×)。
熱壓印成形體之耐撞擊特性,係根據德國汽車工業協會所規定之VDA基準(VDA238-100),在以下測定條件下進行熱壓印成形體之彎曲性的評估。在本發明中,將彎曲試驗中所得之最大荷重時的位移以VDA基準變換為角度,並求出最大彎曲角度。 試驗片尺寸:60mm(軋延方向)×60mm(與軋延呈垂直之方向)、或者30mm(軋延方向)×60mm(與軋延呈垂直之方向) 彎曲稜線:與軋延呈直角的方向 試驗方法:輥支撐、衝頭擠壓 輥徑:φ30mm 衝頭形狀:前端R=0.4mm 輥間距離:2.0×板厚(mm)+0.5mm 擠壓速度:20mm/min 試驗機:SIMAZU AUTOGRAPH 20kN
[實施例A] 磨削具有表1所示化學組成的母材鋼板表面而除去表面氧化物後,於其兩面或單面以電弧熔接積層具有表2所示化學組成的表層用鋼板。此外,電弧熔接後之表層用鋼板與母材鋼板的合計板厚是設為200mm~300mm,且表層用鋼板之厚度是設為母材鋼板厚度的1/3左右(若為單側則是1/4左右)。製造No.1~36及38~40係於兩面上熔接有表層用鋼板的鋼,而製造No.37係僅於單面上熔接有表層用鋼板的鋼。對該積層鋼板施行表3所示熱軋延及/或冷軋延,並對所得之鋼板施行表3所示熱處理來進行熱壓印,而製造出成形體。於表4中顯示熱壓印後之鋼板(熱壓印成形體)之微觀組織及機械特性。此外,將從熱壓印後之鋼板採取之試樣的板厚1/2位置及距表面20μm的位置(表層內的位置)進行分析而得之成分組成,分別與表1及2所示之母材鋼板及表層用鋼板的成分組成為同等。
[表1-1]
[表1-2]
[表2-1]
[表2-2]
[表3-1]
[表3-2]
[表4-1]
[表4-2]
將拉伸強度為1500MPa以上,且最大彎曲角度(°)為70(°)以上,並且耐氫脆化特性合格的情況評估為耐撞擊特性及耐氫脆化特性優異之熱壓印成形體(表4中之實施例)。另一方面,上述3個性能中,只要有任一個未滿足便視為比較例。
[實施例B(Mn:1.50%以上且小於3.00%)] 磨削具有表5所示化學組成的母材鋼板表面而除去表面氧化物後,於其兩面或單面以電弧熔接積層具有表6所示化學組成的表層用鋼板。此外,電弧熔接後之表層用鋼板與母材鋼板的合計板厚是設為200mm~300mm,且表層用鋼板之厚度是設為母材鋼板厚度的1/3左右(若為單側則是1/4左右)。製造No.101~135及137~139係於兩面上熔接有表層用鋼板的鋼,而製造No.136係僅於單面上熔接有表層用鋼板的鋼。對該積層鋼板施行表7所示熱軋延及/或冷軋延,並對所得之鋼板施行表7所示熱處理來進行熱壓印,而製造出成形體。於表8中顯示熱壓印後之鋼板(熱壓印成形體)之微觀組織及機械特性。此外,將從熱壓印後之鋼板採取之試樣的板厚1/2位置及距表面20μm的位置(表層內的位置)進行分析而得之成分組成,分別與表5及6所示之母材鋼板及表層用鋼板的成分組成為同等。
[表5-1]
[表5-2]
[表6-1]
[表6-2]
[表7-1]
[表7-2]
[表8-1]
[表8-2]
局部性之軟化部於撞擊時變形會集中,而成為發生破裂的主要原因,因此成形體中硬度參差小,亦即確保穩定之強度,在確保耐撞擊特性上是很重要的。因此,本實施例中也由硬度參差的觀點來對熱壓印成形體之耐撞擊特性進行了評估。在長條狀之熱壓印成形體的長邊方向上,於任意位置採取與該長邊方向呈垂直的截面,並測定包含縱壁之整個截面區域的板厚中心位置的硬度。測定中係使用維氏試驗機,且測定荷重係設為1kgf,測定間隔設為1mm。令無測定點低於所有測定點之平均值100Hv的情況為硬度參差小,亦即強度穩定性優異,且就結果而言視為耐撞擊特性優異而令其為合格(○),且令具有低100Hv之測定點時為不合格(×)。更具體地來說,令所有測定點之硬度平均值(表8中之平均截面硬度)與所有測定點中最小硬度之值的差在100Hv以下時為合格,且令大於100Hv時為不合格。
與實施例A的情況相同地,將拉伸強度為1500MPa以上,且最大彎曲角度(°)為70(°)以上,並且耐氫脆化特性合格的情況評估為耐撞擊特性及耐氫脆化特性優異之熱壓印成形體(表8中之實施例)。且將平均截面硬度-最少硬度為100Hv以下的情況評估為除彎曲性以外在強度穩定性的觀點上也可改善耐撞擊特性的熱壓印成形體(表8中之實施例111以外的實施例)。另一方面,「拉伸強度」、「最大彎曲角度」及「耐氫脆化特性」之要件中,只要有任一個未滿足便視為比較例。
[實施例C(Si:大於0.50%且小於3.00%)] 磨削具有表9所示化學組成的母材鋼板表面而除去表面氧化物後,於其兩面或單面以電弧熔接積層具有表10所示化學組成的表層用鋼板。此外,電弧熔接後之表層用鋼板與母材鋼板的合計板厚是設為200mm~300mm,且表層用鋼板之厚度是設為母材鋼板厚度的1/3左右(若為單側則是1/4左右)。製造No.201~236及238~240係於兩面上熔接有表層用鋼板的鋼,而製造No.237係僅於單面上熔接有表層用鋼板的鋼。對該積層鋼板施行表11所示熱軋延及/或冷軋延,並對所得之鋼板施行表11所示熱處理來進行熱壓印,而製造出成形體。於表12中顯示熱壓印後之鋼板(熱壓印成形體)之微觀組織及機械特性。此外,將從熱壓印後之鋼板採取之試樣的板厚1/2位置及距表面20μm的位置(表層內的位置)進行分析而得之成分組成,分別與表9及10所示之母材鋼板及表層用鋼板的成分組成為同等。
[表9-1]
[表9-2]
[表10-1]
[表10-2]
[表11-1]
[表11-2]
[表12-1]
[表12-2]
本實施例中,也由延展性的觀點來對熱壓印成形體之耐撞擊特性進行了評估。具體而言,係藉由熱壓印後之鋼板的拉伸試驗求得該鋼板之均勻延伸率,以評估耐撞擊特性。拉伸試驗係製作JIS Z 2201所記載之5號試驗片,並依照JIS Z 2241所記載之試驗方法實施,且令可獲得最大拉伸荷重之延伸率為均勻延伸率。
與實施例A的情況相同地,將拉伸強度為1500MPa以上,且最大彎曲角度(°)為70(°)以上,並且耐氫脆化特性合格的情況評估為耐撞擊特性及耐氫脆化特性優異之熱壓印成形體(表12中之實施例)。且將均勻延伸率為5%以上的情況評估為除彎曲性以外在延展性的觀點上也可改善耐撞擊特性的熱壓印成形體(表12中之實施例210及211以外的實施例)。另一方面,「拉伸強度」、「最大彎曲角度」及「耐氫脆化特性」之要件中,只要有任一個未滿足便視為比較例。
[實施例D(Mn:1.50%以上且小於3.00%及Si:大於0.50%且小於3.00%)] 磨削具有表13所示化學組成的母材鋼板表面而除去表面氧化物後,於其兩面或單面以電弧熔接積層具有表14所示化學組成的表層用鋼板。此外,電弧熔接後之表層用鋼板與母材鋼板的合計板厚是設為200mm~300mm,且表層用鋼板之厚度是設為母材鋼板厚度的1/3左右(若為單側則是1/4左右)。製造No.301~339及341~343係於兩面上熔接有表層用鋼板的鋼,而製造No.340係僅於單面上熔接有表層用鋼板的鋼。對該積層鋼板施行表15所示熱軋延及/或冷軋延,並對所得之鋼板施行表15所示熱處理來進行熱壓印,而製造出成形體。於表16中顯示熱壓印後之鋼板(熱壓印成形體)之微觀組織及機械特性。此外,將從熱壓印後之鋼板採取之試樣的板厚1/2位置及距表面20μm的位置(表層內的位置)進行分析而得之成分組成,分別與表13及14所示之母材鋼板及表層用鋼板的成分組成為同等。
[表13-1]
[表13-2]
[表14-1]
[表14-2]
[表15-1]
[表15-2]
[表16-1]
[表16-2]
本實施例中,與實施例B之情況同樣地,也由硬度參差的觀點來對熱壓印成形體之耐撞擊特性進行了評估。在長條狀之熱壓印成形體的長邊方向上,於任意位置採取與該長邊方向呈垂直的截面,並測定包含縱壁之整個截面區域的板厚中心位置的硬度。測定中係使用維氏試驗機,且測定荷重係設為1kgf,測定間隔設為1mm。令無測定點低於所有測定點之平均值100Hv的情況為硬度參差小,亦即強度穩定性優異,且就結果而言視為耐撞擊特性優異而令其為合格(○),且令具有低100Hv之測定點時為不合格(×)。更具體地來說,令所有測定點之硬度平均值(表16中之平均截面硬度)與所有測定點中最小硬度之值的差在100Hv以下時為合格,且令大於100Hv時為不合格。
而且,本實施例中,與實施例C的情況同樣地,也由延展性的觀點來對熱壓印成形體之耐撞擊特性進行了評估。具體而言,係藉由熱壓印後之鋼板的拉伸試驗求得該鋼板之均勻延伸率,以評估耐撞擊特性。拉伸試驗係製作JIS Z 2201所記載之5號試驗片,並依照JIS Z 2241所記載之試驗方法實施,且令可獲得最大拉伸荷重之延伸率為均勻延伸率。
與實施例A的情況相同地,將拉伸強度為1500MPa以上,且最大彎曲角度(°)為70(°)以上,並且耐氫脆化特性合格的情況評估為耐撞擊特性及耐氫脆化特性優異之熱壓印成形體(表16中之實施例)。且將均勻延伸率為5%以上且平均截面硬度-最少硬度為100Hv以下的情況況評估為除彎曲性以外在延展性及強度穩定性的觀點上也可改善耐撞擊特性的熱壓印成形體(表16中之實施例310、311及313~315以外的實施例)。另一方面,「拉伸強度」、「最大彎曲角度」及「耐氫脆化特性」之要件中,只要有任一個未滿足便視為比較例。
圖1係用以說明製造本發明之高強度鋼板時C原子之擴散的示意圖。 圖2係顯示與製造本發明之高強度鋼板的方法中所使用之粗軋延相關的軋延道次後之差排密度變化的圖表。
Claims (8)
- 一種熱壓印成形體,包含板厚中央部與配置於該板厚中央部的兩側或單側之表層該熱壓印成形體之特徵在於:前述熱壓印成形體更包含中間層,該中間層係形成於前述板厚中央部與各表層之間且與該等相鄰接;前述板厚中央部以質量%計含有:C:0.20%以上且小於0.70%、Si:小於3.00%、Mn:0.20%以上且小於3.00%、P:0.10%以下、S:0.10%以下、sol.Al:0.0002%以上且在3.0000%以下、N:0.01%以下,且剩餘部分由Fe及無法避免之不純物所構成;前述板厚中央部之硬度為500Hv以上且800Hv以下;前述表層之板厚方向的硬度變化△H1為10Hv以上且小於200Hv;前述中間層之板厚方向的硬度變化△H2為50Hv以上且小於200Hv。
- 如請求項1之熱壓印成形體,其中前述板厚中央部之Si含量為0.50%以下,且前述板厚中央部之Mn含量為0.20%以上且小於1.50%。
- 如請求項1之熱壓印成形體,其中前述板厚中央部之Si含量為0.50%以下,且前述板厚中央部之Mn含量為1.50%以上且小於3.00%。
- 如請求項1之熱壓印成形體,其中前述板厚中央部之Si含量為大於0.50%且小於3.00%,前述板厚中央部之Mn含量為0.20%以上且小於1.50%,並且前述板厚中央部以面積分率計包含1.0%以上且小於5.0%的殘留沃斯田鐵。
- 如請求項1之熱壓印成形體,其中前述板厚中央部之Si含量為大於0.50%且小於3.00%,前述板厚中央部之Mn含量為1.50%以上且小於3.00%,並且前述板厚中央部以面積分率計包含1.0%以上且小於5.0%的殘留沃斯田鐵。
- 如請求項1至5中任一項之熱壓印成形體,其中前述板厚中央部以質量%計更含有Ni:0.01%以上且3.00%以下。
- 如請求項1至5中任一項之熱壓印成形體,其中前述板厚中央部以質量%計更含有下述1種或2種以上元素:Nb:0.010%以上且在0.150%以下、Ti:0.010%以上且在0.150%以下、Mo:0.005%以上且在1.000%以下及B:0.0005%以上且在0.0100%以下。
- 如請求項1至5中任一項之熱壓印成形體,其於各表層之表面更包含鍍敷層。
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