WO2012115191A1 - Magnesium alloy and manufacturing method for same - Google Patents

Magnesium alloy and manufacturing method for same Download PDF

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WO2012115191A1
WO2012115191A1 PCT/JP2012/054419 JP2012054419W WO2012115191A1 WO 2012115191 A1 WO2012115191 A1 WO 2012115191A1 JP 2012054419 W JP2012054419 W JP 2012054419W WO 2012115191 A1 WO2012115191 A1 WO 2012115191A1
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Prior art keywords
magnesium alloy
region
plate
plane
rolling
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PCT/JP2012/054419
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French (fr)
Japanese (ja)
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WO2012115191A9 (en
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大石 幸広
森 信之
龍一 井上
河部 望
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住友電気工業株式会社
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Priority to JP2011038889A priority Critical patent/JP5757105B2/en
Priority to JP2011-038889 priority
Application filed by 住友電気工業株式会社 filed Critical 住友電気工業株式会社
Publication of WO2012115191A1 publication Critical patent/WO2012115191A1/en
Publication of WO2012115191A9 publication Critical patent/WO2012115191A9/en

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    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C23/00Alloys based on magnesium
    • C22C23/02Alloys based on magnesium with aluminium as the next major constituent
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B21MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21BROLLING OF METAL
    • B21B3/00Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences Rolling of aluminium, copper, zinc or other non-ferrous metals
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/001Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D11/00Continuous casting of metals, i.e. casting in indefinite lengths
    • B22D11/06Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
    • B22D11/0622Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
    • BPERFORMING OPERATIONS; TRANSPORTING
    • B22CASTING; POWDER METALLURGY
    • B22DCASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B22D21/02Casting exceedingly oxidisable non-ferrous metals, e.g. in inert atmosphere
    • B22D21/04Casting aluminium or magnesium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C23/00Alloys based on magnesium
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22FCHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/06Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of magnesium or alloys based thereon

Abstract

Provided is a magnesium alloy which is thick and exhibits excellent corrosion resistance and excellent surface-deterioration resistance, and a production method for the same. A magnesium (Mg) alloy (typically a magnesium alloy plate) having a plate-shaped section having a thickness of at least 1.5mm, wherein, if the region as far as 1/4 of the thickness, in the thickness direction, from the surface of the plate-shaped section is the surface region, and the remaining section is the inner-section region, the ratio (OF/Oc) of the base surface peak ratio (OF) of the surface region to the base surface peak ratio (Oc) (orientation joint of the (002) surface) of the inner-section region satisfies 1.5<OF/Oc. In this magnesium alloy, the surface of the plate-shaped section is formed by means of an aggregate structure in which the (002) surface, which is the base surface of the Mg alloy crystals, is strongly oriented in comparison with the inner-section, and the alloy exhibits excellent corrosion resistance because the grain size in the surface region is typically smaller than that in the inner-section region, and due to the excellent surface deterioration resistance a molded product having excellent surface quality can be obtained by carrying out press working. A plate-shaped Mg alloy can be obtained by rolling, for a plurality of passes, a twin-roll continuous cast material, with the rolling reduction for all the passes being 25% or less.

Description

マグネシウム合金材及びその製造方法Magnesium alloy material and manufacturing method thereof
 本発明は、自動車や鉄道車両、飛行機などの輸送機器の部品や自転車部品、電子・電気機器の筐体、その他の構造部材といった各種の部材、及び当該部材の構成材料に適したマグネシウム合金材、並びにその製造方法に関するものである。特に、肉厚で、耐食性及び耐肌荒れ性に優れるマグネシウム合金材に関するものである。 The present invention relates to various members such as parts of transportation equipment such as automobiles, railway vehicles, airplanes, bicycle parts, casings of electronic / electric equipment, and other structural members, and magnesium alloy materials suitable for constituent materials of the members, And a manufacturing method thereof. In particular, it relates to a magnesium alloy material that is thick and excellent in corrosion resistance and rough skin resistance.
 携帯電話やノート型パーソナルコンピュータといった携帯用電子・電気機器類の筐体、ホィールカバーやパドルシフトなどの自動車部品、鉄道車両部品、フレームなどの自転車部品といった各種の部材の構成材料として、軽量で、比強度、比剛性に優れるマグネシウム合金が検討されている。マグネシウム合金からなる部材は、ダイカスト法やチクソモールド法による鋳造材(ASTM規格のAZ91合金)が主流である。近年、ASTM規格のAZ31合金に代表される展伸用マグネシウム合金からなる板にプレス加工を施したプレス加工材が使用されつつある。特許文献1では、双ロール鋳造法を用いて、AZ91合金などの各種のマグネシウム合金からなる連続鋳造材を作製し、この連続鋳造材に圧延を施して得られた圧延板にプレス加工を施すことを開示している。 It is lightweight as a component material for various components such as casings for portable electronic and electrical equipment such as mobile phones and notebook personal computers, automobile parts such as wheel covers and paddle shifts, railway vehicle parts, and bicycle parts such as frames. Magnesium alloys excellent in specific strength and specific rigidity have been studied. As for the members made of magnesium alloy, casting materials (ASTM standard AZ91 alloy) by die casting method or thixo mold method are mainly used. In recent years, a press-worked material obtained by press-working a plate made of a magnesium alloy for extension represented by ASTM standard AZ31 alloy is being used. In Patent Document 1, a continuous cast material made of various magnesium alloys such as AZ91 alloy is produced using a twin roll casting method, and a rolled plate obtained by rolling the continuous cast material is subjected to press working. Is disclosed.
国際公開第2006/003899号International Publication No. 2006/003899
 従来、マグネシウム合金の軽量性に着目して、プレス加工材といった塑性加工材の素材には、厚さ1mm以下といった比較的薄い板材が検討されている。しかし、マグネシウム合金の用途範囲の拡大に伴い、上述のような薄板だけでなく、比強度、比剛性に着目して肉厚なもの、具体的には、厚さ1.5mm以上の厚い板材の開発が望まれる。従来、このような肉厚なマグネシウム合金板といった素材、及びその製造方法、並びにこの板を用いて作製したプレス加工材といった塑性加工材について十分に検討されていない。 Conventionally, a relatively thin plate material having a thickness of 1 mm or less has been studied as a material of a plastic work material such as a press work material, focusing on the light weight of a magnesium alloy. However, with the expansion of the range of applications of magnesium alloys, not only the above-mentioned thin plates, but also the development of thick plates with a focus on specific strength and specific rigidity, specifically thick plates with a thickness of 1.5 mm or more Is desired. Conventionally, a material such as a thick magnesium alloy plate, a manufacturing method thereof, and a plastic work material such as a press work material produced using the plate have not been sufficiently studied.
 ダイカスト法やチクソモールド法を利用すれば、肉厚なマグネシウム合金板が得られる。しかし、ダイカスト材といった鋳造材では、巣といった内部欠陥が存在し易い上に、添加元素成分が局所的に高濃度になったり、結晶粒がランダムに配向したりするなど、組成や組織が不均一になり易い。そのため、ダイカスト材といった鋳造材は、圧延材といった塑性加工が施されたものと比較して、耐食性に劣る。また、ダイカスト材といった鋳造材は、上記内部欠陥などにより、塑性加工性に劣り、塑性加工用素材に適すると言えない。 A thick magnesium alloy plate can be obtained by using a die casting method or a thixo mold method. However, in casting materials such as die-cast materials, internal defects such as nests are likely to exist, and the composition and structure are not uniform, such as locally high concentrations of additive element components and random orientation of crystal grains. It is easy to become. Therefore, a cast material such as a die-cast material is inferior in corrosion resistance compared to a cast material such as a rolled material. Further, a cast material such as a die-cast material is inferior in plastic workability due to the above internal defects and cannot be said to be suitable for a material for plastic working.
 そこで、本発明の目的の一つは、肉厚で耐食性及び耐肌荒れ性に優れるマグネシウム合金材や塑性加工が施された肉厚なマグネシウム合金材を提供することにある。また、本発明の他の目的は、肉厚で耐食性及び耐肌荒れ性に優れるマグネシウム合金材が得られるマグネシウム合金材の製造方法を提供することにある。 Therefore, one of the objects of the present invention is to provide a magnesium alloy material that is thick and excellent in corrosion resistance and skin roughness resistance, and a thick magnesium alloy material that has been subjected to plastic working. Another object of the present invention is to provide a method for producing a magnesium alloy material from which a magnesium alloy material that is thick and excellent in corrosion resistance and rough skin resistance can be obtained.
 ダイカスト材やチクソモールド材に比較して、圧延などの塑性加工(1次加工)が施されたマグネシウム合金材は、鋳造時の欠陥が低減されたり、結晶が微細化されたりすることで、同一の組成であっても、強度や硬度、靭性などの機械的特性、耐食性、塑性加工性に優れる。また、上記1次加工を施したマグネシウム合金材にプレス加工などの塑性加工(2次加工)を施したマグネシウム合金材も、上記機械的特性や耐食性に優れる。特に、1次加工材の素材として双ロール鋳造法といった連続鋳造法により製造した連続鋳造材を利用すると、当該連続鋳造材は、偏析や粗大な晶析出物がダイカスト材などに比較して少なく、塑性加工性に優れる。そこで、本発明者らは、連続鋳造材に種々の条件で圧延を施して、厚さ1.5mm以上の肉厚なマグネシウム合金板を作製した。その結果、特定の条件で作製したマグネシウム合金板は、肉厚で、耐食性に優れる上に、プレス加工や曲げ加工といった塑性加工を施した場合、得られた塑性加工材はその表面に凹凸が小さくかつ少なく、滑らかな表面を有しており(代表的には光沢を有して綺麗な表面を有する)、耐肌荒れ性にも優れる、との知見を得た。本発明は、上記知見に基づくものである。 Compared to die-casting materials and thixo-mold materials, magnesium alloy materials that have been subjected to plastic processing (primary processing) such as rolling are the same by reducing defects during casting and making crystals finer. Even with this composition, mechanical properties such as strength, hardness and toughness, corrosion resistance, and plastic workability are excellent. A magnesium alloy material obtained by subjecting the magnesium alloy material subjected to the primary processing to plastic processing (secondary processing) such as press working is also excellent in the mechanical characteristics and corrosion resistance. In particular, when a continuous cast material produced by a continuous casting method such as a twin roll casting method is used as a material for the primary work material, the continuous cast material has less segregation and coarse crystal precipitates than a die cast material, Excellent plastic workability. Therefore, the present inventors rolled the continuous cast material under various conditions to produce a thick magnesium alloy plate having a thickness of 1.5 mm or more. As a result, the magnesium alloy plate produced under specific conditions is thick and excellent in corrosion resistance, and when subjected to plastic working such as press working and bending, the resulting plastic working material has small irregularities on the surface. In addition, it has been found that it has a smooth surface (typically has a glossy and clean surface) and is excellent in rough skin resistance. The present invention is based on the above findings.
 本発明のマグネシウム合金材は、マグネシウム合金からなり、厚さが1.5mm以上の板状部を有し、かつ、この板状部が以下の配向性を満たす。
 [配向性]
 上記板状部の表面から厚さ方向に厚さの1/4までの領域を表面領域、残部の領域を内部領域とし、
 上記表面領域における(002)面、(100)面、(101)面、(102)面、(110)面、及び(103)面のX線回折のピーク強度をそれぞれIF(002)、IF(100)、IF(101)、IF(102)、IF(110)、及びIF(103)とし、
 上記内部領域における(002)面、(100)面、(101)面、(102)面、(110)面、及び(103)面のX線回折のピーク強度をそれぞれIC(002)、IC(100)、IC(101)、IC(102)、IC(110)、及びIC(103)とし、
 上記表面領域における(002)面の配向度合い:IF(002)/{IF(100)+IF(002)+IF(101)+IF(102)+IF(110)+IF(103)}を底面ピーク比OF
 上記内部領域における(002)面の配向度合い:IC(002)/{IC(100)+IC(002)+IC(101)+IC(102)+IC(110)+IC(103)}を底面ピーク比OCとするとき、
 上記内部領域の底面ピーク比Ocに対する上記表面領域の底面ピーク比OFの比率:OF/Ocが、1.05<OF/Ocを満たす。
The magnesium alloy material of the present invention is made of a magnesium alloy, has a plate-like portion having a thickness of 1.5 mm or more, and the plate-like portion satisfies the following orientation.
[Orientation]
The area from the surface of the plate-shaped part to 1/4 of the thickness in the thickness direction is the surface area, the remaining area is the internal area,
The X-ray diffraction peak intensities of the (002) plane, (100) plane, (101) plane, (102) plane, (110) plane, and (103) plane in the surface region are respectively I F (002), I F (100), I F (101), I F (102), I F (110), and I F (103),
The peak intensities of X-ray diffraction of the (002) plane, (100) plane, (101) plane, (102) plane, (110) plane, and (103) plane in the internal region are I C (002), I C (100), I C (101), I C (102), I C (110), and I C (103)
Orientation degree of (002) plane in the surface region: I F (002) / { I F (100) + I F (002) + I F (101) + I F (102) + I F (110) + I F (103)} a bottom peak ratio O F,
Orientation degree of (002) plane in the internal region: I C (002) / {I C (100) + I C (002) + I C (101) + I C (102) + I C (110) + I C (103)} when the the bottom peak ratio O C,
The ratio of the bottom peak ratio O F of the surface area relative to the bottom surface peak ratio O c of the internal region: O F / O c satisfies the 1.05 <O F / O c.
 上記本発明マグネシウム合金材は、例えば、以下の本発明製造方法により製造することができる。本発明のマグネシウム合金材の製造方法は、マグネシウム合金からなる素材に圧延を施してマグネシウム合金材を製造する方法に係るものであり、以下の準備工程と、圧延工程とを具える。
 準備工程:溶解したマグネシウム合金を双ロール鋳造法により連続鋳造した板状の素材を準備する工程。
 圧延工程:上記素材に複数パスの圧延を施して、厚さ1.5mm以上の板状のマグネシウム合金材を製造する工程。
 この圧延工程では、上記各パスの圧下率をいずれも25%以下とする。
 なお、圧下率(%)とは、{(圧延前素材の厚さtb-圧延後の素材の厚さta)/圧延前素材の厚さtb}×100をいう。
The said magnesium alloy material of this invention can be manufactured with the following this invention manufacturing method, for example. The method for producing a magnesium alloy material according to the present invention relates to a method for producing a magnesium alloy material by rolling a material made of a magnesium alloy, and includes the following preparation step and rolling step.
Preparation step: A step of preparing a plate-like material obtained by continuously casting a molten magnesium alloy by a twin roll casting method.
Rolling step: A step of producing a plate-like magnesium alloy material having a thickness of 1.5 mm or more by subjecting the material to rolling in a plurality of passes.
In this rolling process, the rolling reduction of each of the above passes is 25% or less.
The rolling reduction (%) refers to {(thickness t b of raw material before rolling−thickness t a of raw material after rolling) / thickness t b of raw material before rolling} × 100.
 上記本発明製造方法によれば、割れなどの起点となる欠陥や晶析出物、偏析が少ない、或いは実質的に存在しない連続鋳造材を素材とすることで、複数パスの圧延を良好に施すことができる。また、各パスの圧下率を比較的小さくし、かつ複数パスに亘って圧延を施すことで、圧延材の表面部分には内部に比較して、圧延による塑性加工が十分に加えられる。即ち、圧下率が比較的小さい圧延を繰り返し行うことで、圧延材の表面組織と内部組織とを異ならせることができる。従って、本発明製造方法によれば、表面領域を構成する組織と内部領域を構成する組織とが異なる組織により構成されたマグネシウム合金材(代表的には圧延板(本発明マグネシウム合金材の一形態))が得られる。より具体的には、表面領域を構成する組織は、圧延による塑性加工が十分に加えられることで、マグネシウム合金の結晶の底面が圧延方向(圧延される素材が進行する方向)に平行するように主に配列した集合組織(上記結晶のc軸が圧延方向に直交するように配列した集合組織)であり、内部領域を構成する組織は、上記底面が表面領域よりもランダムに配列した組織である。 According to the above-mentioned production method of the present invention, it is possible to satisfactorily perform multiple passes of rolling by using a continuous casting material having few or substantially no defects, crystal precipitates, segregation as a starting point such as cracks, or the like. Can do. In addition, by reducing the rolling reduction of each pass and performing rolling over a plurality of passes, the surface portion of the rolled material is sufficiently subjected to plastic working by rolling as compared with the inside. That is, the surface structure and the internal structure of the rolled material can be made different by repeatedly performing rolling with a relatively small rolling reduction. Therefore, according to the manufacturing method of the present invention, a magnesium alloy material (typically a rolled plate (one form of the magnesium alloy material of the present invention) composed of a structure in which the structure constituting the surface region and the structure constituting the internal region are different. )) Is obtained. More specifically, the structure constituting the surface region is such that the bottom surface of the magnesium alloy crystal is parallel to the rolling direction (the direction in which the material to be rolled proceeds) by sufficiently applying plastic working by rolling. The texture is mainly arranged (texture arranged so that the c-axis of the crystal is orthogonal to the rolling direction), and the structure constituting the inner region is a structure in which the bottom surface is arranged at random than the surface region. .
 本発明マグネシウム合金材が上述の特定の圧延が施された圧延板である場合(即ち、本発明マグネシウム合金材の全体が板状部から構成される形態の場合)、上述のように表面領域の組織が特定の配向性を有する集合組織、より具体的には、マグネシウム合金の結晶の底面である(002)面が強く配向した集合組織であり、内部領域の組織は、この表面領域よりも(002)面の配向が少ない組織により構成される。(002)面が強く配向した集合組織とは、圧延などの塑性加工時に塑性加工に伴う変形が十分に加えられたことを示す指標の一つとなる。圧延などの加工が十分に施されるほど、マグネシウム合金の結晶粒径が微細になる傾向にあり、この微細化により結晶粒界の全面積が増大する。その結果、結晶粒界に対する不純物元素の存在比率が相対的に低下することで、上記特定の組織を有する本発明マグネシウム合金材は耐食性に優れる。特に、外部雰囲気に曝される表面領域が内部よりも微細組織であることで、耐食性により優れる。そのため、本発明マグネシウム合金材は、肉厚で耐食性に優れる。また、このマグネシウム合金材は、上述のように表面部分と内部とで異なる組織から構成されることで、表面部分と内部とで異なる特性(硬度や強度、耐衝撃性、靭性などの機械的特性、耐食性、制振性など)を有する。このような特性差を利用して、本発明マグネシウム合金材は、種々の部材、及びこれらの部材の素材への利用が期待できる。かつ、本発明マグネシウム合金材は、内部領域の底面((002)面)の配向度度合いが小さい(集合組織における集積度が小さい)ことで、プレス加工や曲げ加工といった塑性加工性が良好になることから、プレス加工や曲げ加工といった塑性加工用素材に好適に利用することができる。そして、表面領域が微細な結晶組織で構成されることで、プレス加工などの塑性加工を施しても、素材の表面に大きな凹凸が生じ難く、滑らかな表面を有する塑性加工材(本発明マグネシウム合金材の一形態)が得られる。従って、本発明マグネシウム合金材は、耐肌荒れ性に優れる。また、得られた塑性加工材も優れた表面性状を有する。 When the magnesium alloy material of the present invention is a rolled plate subjected to the specific rolling described above (that is, in the case where the entire magnesium alloy material of the present invention is composed of a plate-shaped portion), as described above, the surface region The texture having a specific orientation, more specifically, a texture in which the (002) plane, which is the bottom surface of the magnesium alloy crystal, is strongly oriented. (002) It is composed of a structure with little orientation of the plane. A texture in which (002) planes are strongly oriented is one of indices indicating that deformation accompanying plastic processing is sufficiently applied during plastic processing such as rolling. As the processing such as rolling is sufficiently performed, the crystal grain size of the magnesium alloy tends to become finer, and this refinement increases the total area of the crystal grain boundary. As a result, the magnesium alloy material of the present invention having the specific structure is excellent in corrosion resistance because the ratio of the impurity element to the crystal grain boundary is relatively lowered. In particular, since the surface region exposed to the external atmosphere has a finer structure than the inside, it is more excellent in corrosion resistance. Therefore, the magnesium alloy material of the present invention is thick and excellent in corrosion resistance. In addition, the magnesium alloy material is composed of different structures in the surface portion and the inside as described above, and thus has different properties (hardness, strength, impact resistance, toughness and other mechanical properties). , Corrosion resistance, vibration control, etc.). Utilizing such a characteristic difference, the magnesium alloy material of the present invention can be expected to be used for various members and materials of these members. In addition, the magnesium alloy material of the present invention has good plastic workability such as press working and bending work because the degree of orientation of the bottom surface ((002) face) of the inner region is small (the degree of integration in the texture is small). Therefore, it can be suitably used for a material for plastic working such as press working or bending. And, since the surface region is composed of a fine crystal structure, even if plastic processing such as press processing is performed, large unevenness is hardly generated on the surface of the material, and the plastic processing material having a smooth surface (the magnesium alloy of the present invention) One form of the material is obtained. Therefore, the magnesium alloy material of the present invention is excellent in rough skin resistance. The obtained plastic work material also has excellent surface properties.
 本発明マグネシウム合金材の一形態として、上記表面領域の平均結晶粒径をDF、上記内部領域の平均結晶粒径をDcとするとき、上記表面領域の平均結晶粒径DFに対する上記内部領域の平均結晶粒径Dcの比率:Dc/DFが、1.5<Dc/DFを満たす形態が挙げられる。 As an embodiment of the magnesium alloy material of the present invention, when the average crystal grain size of the surface region is D F and the average crystal grain size of the internal region is D c , the internal region with respect to the average crystal grain size D F of the surface region is The ratio of the average crystal grain diameter D c in the region: D c / D F satisfies 1.5 <D c / DF .
 上記形態によれば、内部領域の結晶粒径が表面領域よりも大きい、換言すれば、表面領域の結晶粒径が内部領域よりも十分に小さいことで、上述のように結晶粒界が長くなり、耐食性に優れる。また、上記形態によれば、表面領域が微細な結晶組織により構成されることで塑性加工性が良好になる上に耐肌荒れ性に優れ、内側領域の結晶粒径が表面領域よりも大きいことで、耐熱性にも優れる。 According to the above aspect, the crystal grain size of the inner region is larger than the surface region, in other words, the crystal grain size of the surface region is sufficiently smaller than the inner region, so that the crystal grain boundary becomes longer as described above. Excellent corrosion resistance. Further, according to the above form, the surface region is composed of a fine crystal structure, so that the plastic workability is good and the skin roughness resistance is excellent, and the crystal grain size of the inner region is larger than the surface region. Excellent heat resistance.
 本発明マグネシウム合金材の一形態として、上記表面領域のビッカース硬度(Hv)をHF、上記内部領域のビッカース硬度(Hv)をHcとするとき、上記表面領域のビッカース硬度HFに対する上記内部領域のビッカース硬度Hcの比率:Hc/HFが、Hc/HF<0.85を満たす形態が挙げられる。 As one embodiment of the magnesium alloy material of the present invention, when the Vickers hardness (Hv) of the surface region is H F and the Vickers hardness (Hv) of the internal region is H c , the internal to the Vickers hardness H F of the surface region the ratio of the Vickers hardness H c region: H c / H F may include forms that meet the H c / H F <0.85.
 上記形態によれば、内部領域のビッカース硬度が表面領域よりも小さい、換言すれば、表面領域のビッカース硬度が内部領域よりも十分に大きいため、耐摩耗性に優れる。 According to the above embodiment, the Vickers hardness of the inner region is smaller than that of the surface region, in other words, the Vickers hardness of the surface region is sufficiently larger than that of the inner region, so that the wear resistance is excellent.
 本発明マグネシウム合金材は、種々の元素を添加元素とするマグネシウム合金(残部Mg及び不純物)から構成され得る。特に、添加元素の濃度が高い合金、具体的には合計含有量が5.0質量%以上であるマグネシウム合金は、添加元素の種類にもよるが、強度や硬度といった機械的特性、耐食性、難燃性、耐熱性といった種々の特性に優れる。 The magnesium alloy material of the present invention can be composed of magnesium alloys (remainder Mg and impurities) containing various elements as additive elements. In particular, alloys with high concentrations of additive elements, specifically magnesium alloys with a total content of 5.0% by mass or more, depend on the type of additive elements, but mechanical properties such as strength and hardness, corrosion resistance, and flame resistance Excellent in various properties such as heat resistance.
 具体的な添加元素は、Al,Zn,Mn,Si,Be,Ca,Sr,Y,Cu,Ag,Sn,Li,Zr,Ce,Ni,Au及び希土類元素(Y,Ceを除く)から選択される少なくとも1種の元素が挙げられる。不純物は、例えば、Feなどが挙げられる。 Specific additive elements are selected from Al, Zn, Mn, Si, Be, Ca, Sr, Y, Cu, Ag, Sn, Li, Zr, Ce, Ni, Au, and rare earth elements (excluding Y and Ce) And at least one element. Examples of the impurity include Fe.
 特に、Alを含有するMg-Al系合金は、耐食性に優れる上に、強度や硬度といった機械的特性にも優れる。従って、本発明マグネシウム合金材の一形態として、上記マグネシウム合金が添加元素にAlを5.0質量%以上12質量%以下含有する形態が挙げられる。Alの含有量が多いほど上記効果が高い傾向にあり、7質量%以上、更に7.3質量%以上が好ましい。但し、Alの含有量が12質量%を超えると塑性加工性の低下を招くことから、上限は12質量%、更に11質量%が好ましい。特に、Alを8.3質量%~9.5質量%含有する形態は、強度及び耐食性により優れる。Al以外の各元素の含有量は、合計で0.01質量%以上10質量%以下、好ましくは0.1質量%以上5質量%以下が挙げられる。 Especially, Mg-Al alloys containing Al are excellent in corrosion resistance and mechanical properties such as strength and hardness. Therefore, as an embodiment of the magnesium alloy material of the present invention, an embodiment in which the magnesium alloy contains 5.0% by mass or more and 12% by mass or less of Al as an additive element. The higher the Al content, the higher the above effect tends to be. However, if the Al content exceeds 12% by mass, the plastic workability is lowered, so the upper limit is preferably 12% by mass, and more preferably 11% by mass. In particular, the form containing Al of 8.3 mass% to 9.5 mass% is superior in strength and corrosion resistance. The total content of each element other than Al is 0.01% by mass or more and 10% by mass or less, preferably 0.1% by mass or more and 5% by mass or less.
 Mg-Al系合金のより具体的な組成は、例えば、ASTM規格におけるAZ系合金(Mg-Al-Zn系合金、Zn:0.2質量%~1.5質量%、例えば、AZ31合金、AZ61合金、AZ91合金など)、AM系合金(Mg-Al-Mn系合金、Mn:0.15質量%~0.5質量%)、AS系合金(Mg-Al-Si系合金、Si:0.01質量%~20質量%)、Mg-Al-RE(希土類元素)系合金、AX系合金(Mg-Al-Ca系合金、Ca:0.2質量%~6.0質量%)、AJ系合金(Mg-Al-Sr系合金、Sr:0.2質量%~7.0質量%)などが挙げられる。Alを8.3質量%~9.5質量%含有する合金として、更にZnを0.5質量%~1.5質量%含有するMg-Al-Zn系合金、代表的にはAZ91合金が挙げられる。 More specific composition of Mg-Al alloy is, for example, AZ alloy in ASTM standard (Mg-Al-Zn alloy, Zn: 0.2 mass% to 1.5 mass%, for example, AZ31 alloy, AZ61 alloy, AZ91 alloy Etc.), AM alloys (Mg-Al-Mn alloys, Mn: 0.15% to 0.5% by mass), AS alloys (Mg-Al-Si alloys, Si: 0.01% to 20% by mass), Mg -Al-RE (rare earth element) alloy, AX alloy (Mg-Al-Ca alloy, Ca: 0.2 mass% to 6.0 mass%), AJ alloy (Mg-Al-Sr alloy, Sr: 0.2 mass) % To 7.0% by mass). As an alloy containing 8.3 mass% to 9.5 mass% of Al, an Mg-Al-Zn alloy further containing 0.5 mass% to 1.5 mass% of Zn, typically an AZ91 alloy.
 その他、Y,Ce,Ca,Si,Sn及び希土類元素(Y,Ceを除く)から選択される少なくとも1種の元素を合計0.001質量%以上、好ましくは合計0.1質量%以上5質量%以下含有し、残部がMg及び不純物からなるマグネシウム合金は、耐熱性、難燃性に優れる。希土類元素を含有する場合、その合計含有量は0.1質量%以上が好ましく、特に、Yを含有する場合、その含有量は0.5質量%以上が好ましい。 In addition, it contains at least one element selected from Y, Ce, Ca, Si, Sn and rare earth elements (excluding Y and Ce) in a total amount of 0.001% by mass or more, preferably a total of 0.1% by mass or more and 5% by mass or less. The magnesium alloy with the balance being Mg and impurities is excellent in heat resistance and flame retardancy. When the rare earth element is contained, the total content is preferably 0.1% by mass or more, and particularly when Y is contained, the content is preferably 0.5% by mass or more.
 本発明マグネシウム合金材は、肉厚で、耐食性及び耐肌荒れ性に優れる。本発明マグネシウム合金材の製造方法は、肉厚で、耐食性及び耐肌荒れ性に優れるマグネシウム合金材を製造することができる。 The magnesium alloy material of the present invention is thick and excellent in corrosion resistance and rough skin resistance. The production method of the magnesium alloy material of the present invention can produce a magnesium alloy material that is thick and excellent in corrosion resistance and rough skin resistance.
 以下、本発明をより詳細に説明する。
 [マグネシウム合金材]
 (組成)
 本発明マグネシウム合金材は、50質量%以上のMgと、代表的には上述した添加元素とを含有するマグネシウム合金により構成される。
Hereinafter, the present invention will be described in more detail.
[Magnesium alloy material]
(composition)
The magnesium alloy material of the present invention is composed of a magnesium alloy containing 50% by mass or more of Mg and typically the additive elements described above.
 (形態)
 本発明マグネシウム合金材に具える板状部とは、平行する一対の面を具え、両面の間隔(両面の間の距離)が実質的に均一である、即ち、厚さが均一である部分を言う。本発明マグネシウム合金材は、その一部に板状部を有していれば、その他部に、ボスなどが接合された形態、溝を有する形態、表裏に貫通する孔を有する形態など、切削加工などの加工により、局所的に厚さが異なる部分を有する形態を許容する。
(Form)
The plate-like portion provided in the magnesium alloy material of the present invention has a pair of parallel surfaces, and the interval between both surfaces (distance between both surfaces) is substantially uniform, that is, a portion where the thickness is uniform. To tell. If the magnesium alloy material of the present invention has a plate-like part in a part thereof, the cutting process such as a form in which a boss is joined to the other part, a form having a groove, a form having a hole penetrating the front and back, etc. The form which has the part from which thickness differs locally by processing, such as is permitted.
 上記板状部を有する本発明マグネシウム合金材の代表的な形態は、その全体が板状である形態(マグネシウム合金板)が挙げられる。このマグネシウム合金板の形状(平面形状)は、矩形、円形状など種々の形状をとり得る。また、このマグネシウム合金板は、連続する長尺材を巻き取ったコイル材、所定の長さ・形状の短尺材のいずれの形態もとり得る。このマグネシウム合金板は、製造工程によっても種々の形態をとり得る。代表的には、圧延板、圧延板に後述する熱処理や矯正を施した熱処理板や矯正板、上記圧延板や熱処理板、矯正板に研磨や塗装を施した研磨板、塗装板などが挙げられる。 A typical form of the magnesium alloy material of the present invention having the above plate-like portion includes a form (magnesium alloy plate) that is entirely plate-like. The shape (planar shape) of the magnesium alloy plate can take various shapes such as a rectangle and a circle. Moreover, this magnesium alloy plate can take any form of the coil material which wound up the continuous long material, and the short material of predetermined length and shape. This magnesium alloy plate can take various forms depending on the manufacturing process. Typically, a rolled plate, a heat-treated plate or a straightened plate subjected to heat treatment or correction described later, a rolled plate, a heat-treated plate, a polished plate obtained by polishing or coating the straightened plate, a coated plate, or the like can be given. .
 その他、本発明マグネシウム合金材は、上記マグネシウム合金板に、曲げ加工や絞り加工といったプレス加工などの塑性加工(2次加工)を施した成形体、上記塑性加工が一部に施されて、塑性加工部を有する部分加工材が挙げられる(但し、少なくとも一部に上記板状部を有する)。上記成形体は、例えば、天板部(底面部)と、天板部の周縁から立設される側壁部とを有する断面]状の箱体や]状の枠体、天板部が円板状で、側壁部が円筒状の有蓋筒状体などが挙げられる。少なくとも上記天板部が板状部に相当する。所望の用途に応じて、マグネシウム合金材の形態を選択することができる。 In addition, the magnesium alloy material of the present invention is a molded body obtained by subjecting the magnesium alloy sheet to plastic processing (secondary processing) such as press working such as bending or drawing, and the plastic working is partially applied to the plastic. Examples include a partially processed material having a processed part (however, at least a part of the plate-shaped part is included). The molded body is, for example, a cross-sectional box having a top plate portion (bottom surface portion) and a side wall portion erected from the periphery of the top plate portion, a frame-like frame body, and the top plate portion being a disc. For example, a covered cylindrical body having a cylindrical side wall portion may be used. At least the top plate portion corresponds to a plate-like portion. Depending on the desired application, the form of the magnesium alloy material can be selected.
 (厚さ)
 本発明マグネシウム合金材は、上記板状部の厚さが1.5mm以上であることを特徴の一つとする。この厚さは、所望の用途などに応じて、1.5mm以上の任意の値を選択することができる。但し、上記板状部を厚くするには、素材となる鋳造材も厚くする必要がある。鋳造材を厚くすると、上述のように欠陥などで圧延性の低下を招く。従って、上記厚さは10mm以下、特に5mm以下であると、肉厚の圧延板(本発明マグネシウム合金材の一形態)を生産性よく製造できて好ましい。
(thickness)
One feature of the magnesium alloy material of the present invention is that the plate-like portion has a thickness of 1.5 mm or more. As the thickness, an arbitrary value of 1.5 mm or more can be selected according to a desired application. However, in order to increase the thickness of the plate-shaped portion, it is necessary to increase the thickness of the casting material. When the cast material is thickened, the rolling property is deteriorated due to defects as described above. Therefore, it is preferable that the thickness is 10 mm or less, particularly 5 mm or less because a thick rolled plate (one form of the magnesium alloy material of the present invention) can be produced with high productivity.
 本発明マグネシウム合金材が上記成形体や上記部分加工材である場合、塑性加工に伴う変形が少ない箇所(代表的には板状部)は、塑性加工の素材となった上記マグネシウム合金板の組織や機械的特性を概ね維持する。 In the case where the magnesium alloy material of the present invention is the molded body or the partially processed material, the portion where the deformation due to plastic processing is small (typically, the plate-like portion) is the structure of the magnesium alloy plate that is the material of the plastic processing. And generally maintain mechanical properties.
 (組織)
 <配向性>
 本発明マグネシウム合金材は、少なくとも上記板状部の表面領域が上述のように底面の集合組織を有する組織により構成され、内部領域は底面の配向度合いが小さい組織から構成されることを特徴の一つとする。外部雰囲気に曝される表面領域が、(002)面が強く配向した組織により構成されることで上述のように耐食性に優れる。また、表面領域と内部領域とにおいて配向度合いの差が大きいほど、耐食性や表面硬度、耐肌荒れ性を高められると期待される。但し、上記配向度合いの差が大きくなり過ぎると、プレス加工といった塑性加工を均一的に施し難くなるため、上述した底面ピーク比の比率OF/OcはOF/Oc≦1.2を満たすことが好ましい。
(Organization)
<Orientation>
The magnesium alloy material of the present invention is characterized in that at least the surface region of the plate-like portion is composed of a structure having the texture of the bottom surface as described above, and the internal region is composed of a structure having a small degree of orientation of the bottom surface. I will. Since the surface region exposed to the external atmosphere is composed of a structure in which the (002) plane is strongly oriented, the corrosion resistance is excellent as described above. Further, it is expected that the corrosion resistance, the surface hardness, and the rough skin resistance can be improved as the difference in the degree of orientation between the surface region and the inner region increases. However, when the difference between the orientation degree is too large, it becomes difficult subjected to plastic working such as press working uniform, the ratio O F / O c of the above-mentioned bottom peak ratio satisfies the O F / O c ≦ 1.2 Is preferred.
 <平均結晶粒径>
 本発明マグネシウム合金材の代表的な形態では、内部領域の結晶粒径が表面領域よりも大きい形態が挙げられる。この形態は、内部領域が耐熱性に優れ、結晶粒径が相対的に小さい表面領域が上述のように高い耐食性や高い硬度を有する。特に、表面領域が相対的に微細組織であることで、高硬度になり、耐摩耗性に優れることから、キズなどがつき難く、表面性状に優れる。そのため、本発明マグネシウム合金材は、耐久性が求められる構造材などに好適に利用できると期待される。表面領域と内部領域とにおいて平均結晶粒径の差が大きいほど、耐食性や耐肌荒れ性、表面硬度を高められると期待される。但し、上記平均結晶粒径の差が大きくなると、プレス加工といった塑性加工を均一的に施し難くなるため、上述した平均結晶粒径の比率:Dc/DFはDc/DF≦2.0が好ましい。
<Average crystal grain size>
In a typical form of the magnesium alloy material of the present invention, a form in which the crystal grain size of the internal region is larger than that of the surface region can be mentioned. In this form, the internal region is excellent in heat resistance, and the surface region having a relatively small crystal grain size has high corrosion resistance and high hardness as described above. In particular, since the surface region has a relatively fine structure, it has high hardness and excellent wear resistance, so it is difficult to be scratched and has excellent surface properties. Therefore, it is expected that the magnesium alloy material of the present invention can be suitably used for structural materials that require durability. It is expected that the corrosion resistance, the rough skin resistance, and the surface hardness can be increased as the difference in the average crystal grain size between the surface region and the inner region is larger. However, when the difference in the average crystal grain size becomes large, it becomes difficult to uniformly perform plastic working such as press working. Therefore, the ratio of the above average crystal grain size: D c / D F is D c / D F ≦ 2.0 preferable.
 なお、上述のように圧延を施して、厚さが1.5mm以上である肉厚で板状のマグネシウム合金材を製造する場合、厚さ方向の全域に亘って均一的な粒径で、かつ微細な粒径とすることに限界があり、本発明マグネシウム合金材では、表面領域及び内部領域の平均結晶粒径は3.5μm以上となり得る。しかし、結晶粒径が小さいほど、塑性加工性に優れる傾向にあることから、上記板状部の表面領域及び内部領域の平均結晶粒径はいずれも、20μm以下、特に10μm以下が好ましい。平均結晶粒径は、圧延工程における圧下率や素材の加熱温度により変化し、圧下率が大きいほど、また、加熱温度が低いほど、小さくなる傾向にある。 In addition, when producing a thick plate-like magnesium alloy material having a thickness of 1.5 mm or more by rolling as described above, the particle size is uniform and fine throughout the entire thickness direction. In the magnesium alloy material of the present invention, the average crystal grain size in the surface region and the internal region can be 3.5 μm or more. However, since the smaller the crystal grain size, the better the plastic workability, the average crystal grain size of the surface region and the inner region of the plate-like part is preferably 20 μm or less, particularly preferably 10 μm or less. The average crystal grain size varies depending on the rolling reduction in the rolling process and the heating temperature of the material, and tends to be smaller as the rolling reduction is higher and the heating temperature is lower.
 (機械的特性)
 本発明マグネシウム合金材は、圧延が施されていることでダイカスト材などの鋳造材に比較して、強度や硬度、靭性などの機械的特性にも優れる。例えば、上述のように表面領域のビッカース硬度が内部領域よりも高い。表面領域と内部領域とにおいてビッカース硬度の差が大きいほど、表面硬度が相対的に高くなる。但し、上記ビッカース硬度の差が大きくなり過ぎる(表面硬度を大きくし過ぎる)と、逆にプレス加工性を損ねるため、ビッカース硬度(Hv)の比率:Hc/HFは0.7≦Hc/HFが好ましい。ビッカース硬度の絶対値は、圧下率や素材の加熱温度などの圧延条件にもよるが、添加元素の含有量が多いほど、大きくなる傾向にある。本発明マグネシウム合金材が塑性加工材(成形体)や部分加工材である場合、加工硬化により、硬度が更に高まる傾向にある。
(Mechanical properties)
The magnesium alloy material of the present invention is excellent in mechanical properties such as strength, hardness and toughness as compared with a cast material such as a die-cast material because of being rolled. For example, as described above, the Vickers hardness of the surface region is higher than that of the internal region. The greater the difference in Vickers hardness between the surface region and the inner region, the higher the surface hardness. However, if the above Vickers hardness difference is too large (surface hardness is too large), press workability is adversely affected, so the ratio of Vickers hardness (Hv): H c / H F is 0.7 ≦ H c / H F is preferred. Although the absolute value of the Vickers hardness depends on rolling conditions such as the rolling reduction and the heating temperature of the material, the absolute value of Vickers hardness tends to increase as the content of the additive element increases. When the magnesium alloy material of the present invention is a plastically processed material (molded body) or a partially processed material, the hardness tends to further increase due to work hardening.
 (その他の構成)
 本発明マグネシウム合金材の表面の少なくとも一部に化成処理や陽極酸化処理といった防食処理を施して防食層を具える形態とすると、耐食性により優れる。また、本発明マグネシウム合金材の表面の少なくとも一部に塗装を施して塗装層とを具える形態とすると、意匠性や商品価値を高められる。
(Other configurations)
If the anticorrosive treatment such as chemical conversion treatment or anodizing treatment is performed on at least a part of the surface of the magnesium alloy material of the present invention to provide an anticorrosion layer, the corrosion resistance is excellent. Moreover, if it is set as the form which provides a coating layer by coating at least one part of the surface of this invention magnesium alloy material, designability and commercial value can be improved.
 [製造方法]
 以下、上述した本発明製造方法の各工程をより詳細に説明する。
  (準備工程)
 <鋳造>
 本発明製造方法では、出発材に連続鋳造材を利用する。連続鋳造法は、急冷凝固が可能であるため、添加元素の含有量が多い場合でも偏析や酸化物などを低減でき、割れの起点になり得る10μm超といった粗大な晶析出物の生成を抑制できる。従って、圧延などの塑性加工性に優れる鋳造材が得られる。また、連続鋳造法では、長尺な鋳造材を連続して製造可能であり、当該連続鋳造法によって得られた長尺材を圧延の素材に利用できる。素材が長尺である場合、長尺な圧延材を製造可能である。連続鋳造法には、双ロール法、ツインベルト法、ベルトアンドホイール法といった種々の方法があるが、板状の鋳造材の製造には、双ロール法やツインベルト法、特に双ロール法が好適であり、とりわけ特許文献1に記載の鋳造方法で製造した連続鋳造材を利用することが好ましい。鋳造材の厚さ、幅、長さは所望の圧延材(圧延板)が得られるように適宜選択することができる。鋳造材の厚さは、厚過ぎると偏析が生じ易いため、10mm以下、特に5mm以下が好ましい。得られた連続鋳造材を長尺材とする場合、円筒状に巻き取ってコイル材とすると、次工程に搬送し易い。鋳造材における巻き取り直前の箇所を100℃~200℃程度に加熱した状態で巻き取ると、AZ91合金といった添加元素の含有量が高く、割れが生じ易い合金種であっても曲げ易くなり、巻き取り径が小さい場合でも、割れなどを生じることなく巻き取れる。得られた連続鋳造材を適宜な長さに切断したシート材を圧延の素材とすることもできる。この場合、所定の長さの圧延材(圧延板)が得られる。
[Production method]
Hereafter, each process of the manufacturing method of this invention mentioned above is demonstrated in detail.
(Preparation process)
<Casting>
In the production method of the present invention, a continuous casting material is used as a starting material. Since the continuous casting method can be rapidly solidified, segregation and oxides can be reduced even when the content of additive elements is large, and the formation of coarse crystal precipitates exceeding 10 μm that can be the starting point of cracking can be suppressed. . Therefore, a cast material excellent in plastic workability such as rolling can be obtained. In the continuous casting method, a long cast material can be continuously produced, and the long material obtained by the continuous casting method can be used as a rolling material. When the material is long, a long rolled material can be manufactured. There are various continuous casting methods such as a twin roll method, a twin belt method, and a belt-and-wheel method, but the twin roll method and the twin belt method, particularly the twin roll method are suitable for the production of a plate-shaped cast material. In particular, it is preferable to use a continuous cast material produced by the casting method described in Patent Document 1. The thickness, width, and length of the cast material can be appropriately selected so that a desired rolled material (rolled plate) can be obtained. Since the thickness of the cast material is likely to be segregated if it is too thick, it is preferably 10 mm or less, particularly preferably 5 mm or less. When the obtained continuous cast material is a long material, it is easy to transport to the next step if it is wound into a cylindrical shape to form a coil material. If the part immediately before winding in the cast material is wound in a state heated to about 100 ° C to 200 ° C, the content of additive elements such as AZ91 alloy is high, and even an alloy type that is prone to cracking becomes easy to bend. Even when the take-up diameter is small, it can be wound up without causing cracks. A sheet material obtained by cutting the obtained continuous cast material into an appropriate length can be used as a rolling material. In this case, a rolled material (rolled sheet) having a predetermined length is obtained.
 <溶体化>
 上記鋳造材に圧延を施す前に溶体化処理を施すと、鋳造材の組成を均質化したり、Alといった元素を十分に固溶させて靭性を高めたりできる。溶体化処理の条件は、例えば、加熱温度:350℃以上、特に380℃以上420℃以下、保持時間:1時間以上40時間以下が挙げられる。Mg-Al系合金である場合、Alの含有量が多いほど保持時間を長めにすることが好ましい。また、上記保持時間経過後、上記加熱温度からの冷却工程において、水冷や衝風といった強制冷却などを利用して、冷却速度を速めると(好ましくは50℃/min以上)、粗大な析出物の析出を抑制できる。
<Solution>
When the solution treatment is performed before rolling the cast material, the composition of the cast material can be homogenized or the toughness can be enhanced by sufficiently dissolving an element such as Al. Examples of the solution treatment conditions include heating temperature: 350 ° C. or higher, particularly 380 ° C. or higher and 420 ° C. or lower, holding time: 1 hour or longer and 40 hours or shorter. In the case of an Mg—Al-based alloy, it is preferable that the holding time be longer as the Al content is higher. Further, after the holding time has elapsed, in the cooling process from the heating temperature, using forced cooling such as water cooling or blast, the cooling rate is increased (preferably 50 ° C./min or more), so that coarse precipitates Precipitation can be suppressed.
 <圧延>
 上記鋳造材や溶体化処理材を素材とし、この素材に複数パスの圧延を施す。少なくとも1パスは、素材(鋳造材や溶体化処理材、圧延途中の加工材)を150℃以上400℃以下に加熱して行う温間圧延、或いは熱間圧延を含むことが好ましい。素材を上記温度に加熱することで、1パスあたりの圧下率を高めた場合にも圧延中に割れなどが生じ難く、上記温度を高めるほど、割れなどが少なくなり、400℃以下とすることで、素材表面の焼付きなどによる劣化や、圧延ロールの熱劣化を抑制することができる。従って、上記加熱温度は、350℃以下、更に300℃以下、特に150℃以上280℃以下が好ましい。素材だけでなく圧延ロールも加熱してもよい。圧延ロールの加熱温度は、100℃~250℃が挙げられる。
<Rolling>
The cast material or solution treatment material is used as a raw material, and this material is subjected to multiple passes of rolling. It is preferable that at least one pass includes warm rolling or hot rolling performed by heating a raw material (a cast material, a solution treatment material, a processed material during rolling) to 150 ° C. or more and 400 ° C. or less. By heating the material to the above temperature, even when the rolling reduction per pass is increased, cracks and the like are less likely to occur during rolling, and the higher the temperature, the less the cracks, etc. Deterioration due to seizure of the material surface and thermal deterioration of the rolling roll can be suppressed. Therefore, the heating temperature is preferably 350 ° C. or lower, more preferably 300 ° C. or lower, and particularly preferably 150 ° C. or higher and 280 ° C. or lower. You may heat not only a raw material but a rolling roll. Examples of the heating temperature of the rolling roll include 100 ° C. to 250 ° C.
 特に、本発明製造方法では、各パスの圧下率を全て25%以下とする。圧下率が比較的小さい圧延を複数パスに亘って施すことで、特に、素材の表面部分に集中的に塑性加工を施せる。各パスの圧下率は、25%以下の範囲で適宜選択することができるが、小さ過ぎると所望の厚さにするまでのパス数が多くなり、生産性の低下を招くことから、10%以上が好ましい。 In particular, in the manufacturing method of the present invention, the rolling reduction rate of each pass is 25% or less. By performing rolling with a relatively small rolling reduction over a plurality of passes, it is possible to perform plastic processing in a concentrated manner especially on the surface portion of the material. The rolling reduction ratio of each pass can be selected as appropriate within a range of 25% or less, but if it is too small, the number of passes until the desired thickness is increased, resulting in a decrease in productivity. Is preferred.
 パスごとに、素材の加熱温度や圧延ロールの温度、圧下率などの条件を変更することができる。従って、各パスの圧下率は同じでもよいし、異ならせてもよい。また、パス間に中間熱処理を行ってもよい。中間熱処理を行うことで、当該熱処理までに素材に導入された歪みや残留応力などを除去・低減して、当該熱処理以降の圧延を施し易くすることができる。中間熱処理の条件は、加熱温度:150℃~350℃(好ましくは300℃以下、より好ましくは250℃~280℃)、保持時間:0.5時間~3時間)が挙げられる。また、圧延後にも上記条件で最終熱処理を行ってもよい。その他、上記圧延は、潤滑剤を適宜利用すると、圧延時の摩擦抵抗を低減でき、素材の焼き付きなどを防止して、圧延を施し易い。 ∙ Conditions such as the heating temperature of the material, the temperature of the rolling roll, and the rolling reduction can be changed for each pass. Therefore, the rolling reduction rate of each pass may be the same or different. Further, intermediate heat treatment may be performed between passes. By performing the intermediate heat treatment, it is possible to remove and reduce distortions, residual stresses, and the like introduced into the material before the heat treatment, and to easily perform rolling after the heat treatment. The conditions for the intermediate heat treatment include heating temperature: 150 ° C. to 350 ° C. (preferably 300 ° C. or less, more preferably 250 ° C. to 280 ° C., holding time: 0.5 hour to 3 hours). Moreover, you may perform final heat processing on the said conditions after rolling. In addition, in the above rolling, when a lubricant is appropriately used, the frictional resistance during rolling can be reduced, and the material can be prevented from being seized and easily rolled.
 その他、圧延前の鋳造材の縁部をトリミングして、圧延時、縁部に割れが存在した場合にその割れが進展しないようにしてもよいし、圧延工程の途中、圧延後などにおいて、幅を適宜調整するためにトリミングしてもよい。 In addition, the edge of the cast material before rolling may be trimmed to prevent the crack from progressing when the edge is cracked during rolling. You may trim in order to adjust suitably.
 <その他の加工>
  ≪研磨≫
 上記圧延後、研磨を施してもよい。研磨を行うことで、圧延時に使用した潤滑剤や圧延材表面に存在するキズや酸化膜などを除去、低減できる。研磨には、研削ベルトを用いると、素材が長尺材であっても、連続して容易に研磨を施せて好ましい。また、研磨は、粉末の飛散を防止するために湿式が好ましい。
<Other processing>
≪Polishing≫
You may grind | polish after the said rolling. By polishing, it is possible to remove and reduce the lubricant used during rolling, scratches and oxide films present on the surface of the rolled material, and the like. For the polishing, it is preferable to use a grinding belt because it can be easily and continuously polished even if the material is a long material. The polishing is preferably wet in order to prevent the powder from scattering.
  ≪矯正≫
 上記圧延後や上記研磨後、矯正を施してもよい。矯正を行うことで平坦性を高められ、プレス加工などの塑性加工を精度良く行える。矯正には、複数のローラが千鳥状に配置されたロールレベラ装置を好適に利用できる。また、矯正は、例えば、素材を100℃~300℃、特に150℃~280℃に加熱した状態(温間矯正)で行ってもよい。
≪Correction≫
Correction may be performed after the rolling or after the polishing. By performing the correction, the flatness can be improved, and plastic processing such as press processing can be performed with high accuracy. For correction, a roll leveler device in which a plurality of rollers are arranged in a staggered manner can be suitably used. The correction may be performed, for example, in a state where the material is heated to 100 ° C. to 300 ° C., particularly 150 ° C. to 280 ° C. (warm correction).
  ≪塑性加工≫
 上記本発明マグネシウム合金材を成形体や塑性加工部を具える部分加工材とする場合、上述した圧延工程を経た素材(上述した圧延材、研磨材、矯正材)の少なくとも一部にプレス加工といった塑性加工を施す塑性加工工程を具える製造方法により、製造することができる。この塑性加工は、200℃~300℃の温度域で行うと、素材の塑性加工性を高められて好ましい。また、この塑性加工後に熱処理を施して、塑性加工により導入された歪みや残留応力の除去、機械的特性の向上を図ることができる。この熱処理条件は、加熱温度:100℃~300℃、加熱時間:5分~60分程度が挙げられる。
≪Plastic processing≫
When the magnesium alloy material of the present invention is a partially processed material having a molded body or a plastic processing portion, at least a part of the material that has undergone the rolling process described above (rolled material, abrasive material, correction material described above) and so on. It can be manufactured by a manufacturing method including a plastic processing step for performing plastic processing. This plastic working is preferably performed at a temperature range of 200 ° C. to 300 ° C., because the plastic workability of the material is improved. In addition, heat treatment can be performed after the plastic working to remove strain and residual stress introduced by the plastic working and to improve the mechanical characteristics. The heat treatment conditions include a heating temperature: 100 ° C. to 300 ° C. and a heating time: about 5 minutes to 60 minutes.
  ≪表面処理≫
 上記本発明マグネシウム合金材を上記防食層や塗装層を具える形態とする場合、上述した圧延工程を経た素材の少なくとも一部、或いは上記塑性加工工程を経た素材の少なくとも一部に防食処理や塗装を施す表面処理工程を具える製造方法により、製造することができる。その他、上記素材の少なくとも一部に、ヘアライン加工、ダイヤカット加工、ショットブラスト加工、エッチング加工及びスピンカット加工から選択される少なくとも1種の加工を施してもよい。これらの表面処理を行うことで、耐食性や機械的保護機能を高めたり、意匠性や金属質感、商品価値を高めたりすることができる。
≪Surface treatment≫
When the magnesium alloy material of the present invention is provided with the anticorrosion layer and the coating layer, at least a part of the material that has undergone the rolling process described above, or at least a part of the material that has undergone the plastic working process, It can manufacture by the manufacturing method which comprises the surface treatment process which performs. In addition, at least one kind of processing selected from hairline processing, diamond cutting processing, shot blasting processing, etching processing, and spin cutting processing may be applied to at least a part of the material. By performing these surface treatments, corrosion resistance and mechanical protection functions can be improved, and design properties, metal texture, and commercial value can be increased.
 以下、試験例を挙げて、本発明のより具体的な実施の形態を説明する。
 [試験例]
 以下の組成のマグネシウム合金からなる素材に、種々の条件で圧延を施して厚さ1.5mm以上のマグネシウム合金板を作製し、配向性、結晶粒径、及びビッカース硬度を調べた。
Hereinafter, more specific embodiments of the present invention will be described with reference to test examples.
[Test example]
A material composed of a magnesium alloy having the following composition was rolled under various conditions to produce a magnesium alloy plate having a thickness of 1.5 mm or more, and the orientation, crystal grain size, and Vickers hardness were examined.
 この試験では、AZ91合金相当の組成を有するマグネシウム合金(Mg-9.0質量%Al-0.6質量%Zn)からなるマグネシウム合金板と、AZ31合金相当の組成を有するマグネシウム合金(Mg-3.1質量%Al-0.7質量%Zn)からなるマグネシウム合金板とを作製した。 In this test, a magnesium alloy plate made of a magnesium alloy (Mg-9.0 mass% Al-0.6 mass% Zn) having a composition equivalent to AZ91 alloy, and a magnesium alloy (Mg-3.1 mass% Al--) having a composition equivalent to AZ31 alloy. A magnesium alloy plate made of 0.7 mass% Zn) was produced.
 上記各組成のマグネシウム合金を用いて、双ロール連続鋳造法により長尺な鋳造板(厚さ4.5mm(4.50mm~4.51mm)×幅320mm)を作製して、一旦巻き取り、鋳造コイル材を作製した。各鋳造コイル材に400℃×24時間の溶体化処理を施した。溶体化処理を施した固溶コイル材を巻き戻した素材に、表1に示す圧延条件で複数パスの圧延を施し、厚さ2.0mm(2.00mm~2.01mm)又は1.5mmの圧延材(マグネシウム合金板)を作製した。各パスは温間圧延とした(素材の加熱温度:250℃~280℃、圧延ロールの温度:100℃~250℃)。鋳造材の厚さ、圧延途中の加工材の厚さ、得られたマグネシウム合金板の厚さはいずれも、測定対象となる板材の幅方向の中央部、及び幅方向の両縁から50mmの地点の合計3点の厚さの平均とした。 Using the magnesium alloy of the above composition, create a long cast plate (thickness 4.5mm (4.50mm to 4.51mm) x width 320mm) by twin-roll continuous casting method, and wind it up once to obtain the cast coil material. Produced. Each cast coil material was subjected to a solution treatment at 400 ° C. for 24 hours. The material obtained by rewinding the solid solution coil material that has undergone solution treatment is rolled in multiple passes under the rolling conditions shown in Table 1, and rolled material with a thickness of 2.0 mm (2.00 mm to 2.01 mm) or 1.5 mm (magnesium) Alloy plate) was prepared. Each pass was warm-rolled (material heating temperature: 250 ° C to 280 ° C, rolling roll temperature: 100 ° C to 250 ° C). The thickness of the cast material, the thickness of the processed material in the middle of rolling, and the thickness of the obtained magnesium alloy plate are all 50 mm from the center in the width direction of the plate to be measured and both edges in the width direction. It was set as the average of the thickness of a total of three points.
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000001
 [配向性]
 得られた各マグネシウム合金板についてX線回折を行い、内部領域の底面ピーク比Ocに対する表面領域の底面ピーク比OFの比率:OF/Ocを調べた。その結果を表2に示す。表面領域の底面ピーク比OFは、各マグネシウム合金板の表面に対してX線回折を行い、内部領域の底面ピーク比Ocは、各マグネシウム合金板の表面から厚さ方向に厚さの1/4までの領域(表面領域)を化学的に除去して、内部を露出させ、この露出面に対してX線回折を行った。そして、各領域の(002)面、(100)面、(101)面、(102)面、(110)面、及び(103)面のピーク強度をそれぞれ測定し、この測定結果を利用してOF/Ocを求めた。
 底面ピーク比OF:IF(002)/{IF(100)+IF(002)+IF(101)+IF(102)+IF(110)+IF(103)}
 底面ピーク比OC:IC(002)/{IC(100)+IC(002)+IC(101)+IC(102)+IC(110)+IC(103)}
[Orientation]
For each of the obtained magnesium alloy plate subjected to X-ray diffraction, the ratio of the bottom peak ratio O F surface area relative to the bottom surface peak ratio O c of the inner region was investigated with O F / O c. The results are shown in Table 2. Bottom peak ratio O F surface area, subjected to X-ray diffraction with respect to the surface of the magnesium alloy plate, the bottom peak ratio O c of the inner region, the first surface from the thickness in the thickness direction of the magnesium alloy plate The region up to / 4 (surface region) was chemically removed to expose the interior, and X-ray diffraction was performed on this exposed surface. And measure the peak intensity of (002) plane, (100) plane, (101) plane, (102) plane, (110) plane, and (103) plane of each region, and use this measurement result. to determine the O F / O c.
Bottom peak ratio O F: I F (002) / {I F (100) + I F (002) + I F (101) + I F (102) + I F (110) + I F (103)}
Bottom peak ratio O C : I C (002) / {I C (100) + I C (002) + I C (101) + I C (102) + I C (110) + I C (103)}
 [平均結晶粒径]
 得られた各マグネシウム合金板について内部領域及び表面領域の平均結晶粒径(μm)を「鋼-結晶粒度の顕微鏡試験方法 JIS G 0551(2005)」に基づいて測定した。ここでは、各マグネシウム合金板に対して厚さ方向の断面(横断面及び縦断面)をとり、各断面を光学顕微鏡で観察し(400倍)、上記各断面における表面領域(表面から厚さ方向に厚さの1/4までの領域)、及び内部領域(表面領域を除いた残部の領域)のそれぞれについて3視野ずつとり(各領域の合計視野数:6)、視野ごとに平均結晶粒径を求めた。表面領域における合計6視野の平均結晶粒径の平均値(DF)、内部領域における合計6視野の平均結晶粒径の平均値(DC)を表2に示す。また、表面領域の平均結晶粒径DFに対する内部領域の平均結晶粒径Dcの比率:Dc/DFも求めた。その結果を表2に示す。
[Average grain size]
For each of the obtained magnesium alloy plates, the average crystal grain size (μm) of the inner region and the surface region was measured based on “steel—microscopic test method of crystal grain size JIS G 0551 (2005)”. Here, a cross section in the thickness direction (cross section and longitudinal section) is taken for each magnesium alloy plate, each cross section is observed with an optical microscope (400 times), and the surface region in each cross section (from the surface to the thickness direction) 3 areas (up to 1/4 of the thickness) and internal areas (remaining areas excluding the surface area), 3 fields of view (total number of fields of view: 6), average grain size for each field of view Asked. Table 2 shows the average value (D F ) of the average crystal grain size of a total of six views in the surface region and the average value (D C ) of the average crystal grain size of a total of six views in the internal region. Further, the ratio of the average crystal grain size D c in the inner region to the average crystal grain size D F in the surface region: D c / DF was also obtained. The results are shown in Table 2.
 [ビッカース硬度]
 得られた各マグネシウム合金板について内部領域及び表面領域のビッカース硬度(Hv)を調べた。ビッカース硬度は、平均結晶粒径の測定と同様に、各マグネシウム合金板に対して厚さ方向の断面(横断面及び縦断面)をとり、表面領域のビッカース硬度HFは、上記各断面における表面領域に圧子を押し当てて測定し、内部領域のビッカース硬度Hcは、上記各断面における内部領域に圧子を押し当てて測定した。表面領域における上記両断面のビッカース硬度の平均値(HF)、内部領域における上記両断面のビッカース硬度の平均値(HC)を表2に示す。また、表面領域のビッカース硬度HFに対する内部領域のビッカース硬度Hcの比率:Hc/HFも求めた。その結果を表2に示す。
[Vickers hardness]
The Vickers hardness (Hv) of the internal region and the surface region was examined for each obtained magnesium alloy plate. Vickers hardness, as with the measurement of the average crystal grain size, taken in the thickness direction of the cross section (cross section and longitudinal section) for each magnesium alloy plates, Vickers hardness H F in the surface region, the surface of each section measured by pressing an indenter to the area, the Vickers hardness H c of the internal region was measured by pressing an indenter to the internal area of each cross section. Table 2 shows the average value (H F ) of the Vickers hardness of both cross sections in the surface region and the average value (H C ) of the Vickers hardness of both cross sections in the internal region. The ratio of the Vickers hardness H c of the inner region to the Vickers hardness H F of the surface area: H c / H F was also determined. The results are shown in Table 2.
 [腐食試験]
 得られた各マグネシウム合金板について耐食性を調べた。ここでは、JIS Z 2371(2000)に準拠して試験片を作製して(厚さは作製した板厚とした)、96時間の塩水噴霧試験を行い、試験後の腐食減量(mg/cm2)を調べた。その結果を表2に示す。
[Corrosion test]
Each magnesium alloy plate obtained was examined for corrosion resistance. Here, a test piece was prepared in accordance with JIS Z 2371 (2000) (the thickness was the thickness of the prepared plate), a 96-hour salt spray test was performed, and the corrosion weight loss after the test (mg / cm 2 ) Was investigated. The results are shown in Table 2.
Figure JPOXMLDOC01-appb-T000002
Figure JPOXMLDOC01-appb-T000002
 表1,2に示すように、連続鋳造材に、1パスあたりの圧下率が25%以下の圧延を複数パスに亘って施すことで、厚さ1.5mm以上の肉厚のマグネシウム合金板(マグネシウム合金材)であって、その厚さ方向における内部領域の組織(底面ピーク比)と表面領域の組織(底面ピーク比)とが異なるものが得られることが分かる。また、このマグネシウム合金板は、上記内部領域の機械的特性と表面領域の機械的特性とが異なることが分かる。 As shown in Tables 1 and 2, the continuous cast material is rolled with a rolling reduction of 25% or less per pass over multiple passes, so that a magnesium alloy plate with a thickness of 1.5 mm or more (magnesium It can be seen that an alloy material) having an internal region structure (bottom peak ratio) and a surface region structure (bottom peak ratio) in the thickness direction is different. It can also be seen that this magnesium alloy plate has different mechanical properties in the internal region and in the surface region.
 得られた各マグネシウム合金板にプレス加工を施したところ(マグネシウム合金板の加熱温度:250℃~270℃)、いずれの試料もプレス加工を施すことができた。また、得られた各プレス加工材において平坦な部分の組織を調べたところ、プレス加工前の各マグネシウム合金板の組織と実質的に同様であり、同様な底面ピーク比や平均結晶粒径を有していた。更に、得られた各プレス加工材において、曲げ加工部分の表面粗さRaを調べた。その結果を表2に示す。表面領域と内部領域とで異なる組織を有する試料、具体的には表面領域の粒径が大きい組織から構成された試料No.B,C,E,F,H,I,K,Lは、表面粗さRaが概ね0.5μm以下と小さく、滑らかな表面を有することが分かる。 When each of the obtained magnesium alloy plates was pressed (heating temperature of the magnesium alloy plate: 250 ° C. to 270 ° C.), all the samples could be pressed. Further, when the structure of the flat portion of each obtained pressed material was examined, it was substantially the same as the structure of each magnesium alloy plate before pressing, and had the same bottom surface peak ratio and average grain size. Was. Furthermore, the surface roughness Ra of the bent portion of each obtained press-worked material was examined. The results are shown in Table 2. Samples with different structures in the surface area and the inner area, specifically, samples No. B, C, E, F, H, I, K, and L, which are composed of structures with a large particle size in the surface area, It can be seen that the roughness Ra is as small as about 0.5 μm or less and has a smooth surface.
 上記試験結果から、厚さ1.5mm以上の肉厚の板状部をを有するマグネシウム合金材であって、当該板状部の組織が厚さ方向に異なっており、かつ特定の配向性を有する組織から構成されたものは、耐肌荒れ性に優れることが確認された。また、表面領域が相対的に微細組織から構成されることでこのマグネシウム合金材は、耐食性に優れることが確認された。 From the above test results, a magnesium alloy material having a plate-like portion with a thickness of 1.5 mm or more, the structure of the plate-like portion being different in the thickness direction, and having a specific orientation It was confirmed that the material composed of was excellent in rough skin resistance. Moreover, it was confirmed that this magnesium alloy material is excellent in corrosion resistance because the surface region is composed of a relatively fine structure.
 なお、上述した実施形態は、本発明の要旨を逸脱することなく、適宜変更することが可能であり、上述した構成に限定されるものではない。例えば、マグネシウム合金の組成、マグネシウム合金材の厚さ・形状、圧延工程における各パスの圧下率、パス数などを適宜変更することができる。 It should be noted that the above-described embodiment can be appropriately changed without departing from the gist of the present invention, and is not limited to the above-described configuration. For example, the composition of the magnesium alloy, the thickness and shape of the magnesium alloy material, the rolling reduction of each pass in the rolling process, the number of passes, and the like can be changed as appropriate.
 本発明マグネシウム合金材は、自動車部品、鉄道車両部品、航空機部品、自転車部品、各種の電子・電気機器類の部品など、特に耐食性や耐摩耗性が望まれる種々の分野の部材、及び当該部材の構成材料、カバンなどやその素材に好適に利用することができる。本発明マグネシウム合金材の製造方法は、上記本発明マグネシウム合金材の製造に好適に利用することができる。 The magnesium alloy material of the present invention is a member of various fields in which corrosion resistance and wear resistance are particularly desired, such as automobile parts, railway vehicle parts, aircraft parts, bicycle parts, parts of various electronic and electrical devices, and the like. It can be suitably used as a constituent material, a bag, or the like. The manufacturing method of this invention magnesium alloy material can be utilized suitably for manufacture of the said this invention magnesium alloy material.

Claims (5)

  1.  マグネシウム合金からなり、板状部を有するマグネシウム合金材であって、
     前記板状部の厚さが1.5mm以上であり、
     前記板状部は、以下の配向性を満たすことを特徴とするマグネシウム合金材。
     [配向性]
     前記板状部の表面から厚さ方向に厚さの1/4までの領域を表面領域、残部を内部領域とし、
     前記表面領域における(002)面、(100)面、(101)面、(102)面、(110)面、及び(103)面のX線回折のピーク強度をそれぞれIF(002)、IF(100)、IF(101)、IF(102)、IF(110)、及びIF(103)とし、
     前記内部領域における(002)面、(100)面、(101)面、(102)面、(110)面、及び(103)面のX線回折のピーク強度をそれぞれIC(002)、IC(100)、IC(101)、IC(102)、IC(110)、及びIC(103)とし、
     前記表面領域における(002)面の配向度合い:IF(002)/{IF(100)+IF(002)+IF(101)+IF(102)+IF(110)+IF(103)}を底面ピーク比OF
     前記内部領域における(002)面の配向度合い:IC(002)/{IC(100)+IC(002)+IC(101)+IC(102)+IC(110)+IC(103)}を底面ピーク比OCとするとき、
     前記内部領域の底面ピーク比Ocに対する前記表面領域の底面ピーク比OFの比率:OF/Ocが、1.05<OF/Ocを満たす。
    A magnesium alloy material made of a magnesium alloy and having a plate-like portion,
    The thickness of the plate-like portion is 1.5 mm or more,
    The said plate-shaped part satisfy | fills the following orientation, The magnesium alloy material characterized by the above-mentioned.
    [Orientation]
    The area from the surface of the plate-like part to 1/4 of the thickness in the thickness direction is the surface area, the remainder is the internal area,
    The X-ray diffraction peak intensities of the (002) plane, (100) plane, (101) plane, (102) plane, (110) plane, and (103) plane in the surface region are I F (002), I F (100), I F (101), I F (102), I F (110), and I F (103),
    The X-ray diffraction peak intensities of the (002) plane, (100) plane, (101) plane, (102) plane, (110) plane, and (103) plane in the internal region are respectively I C (002), I C (100), I C (101), I C (102), I C (110), and I C (103)
    Orientation degree of (002) plane in the surface region: I F (002) / { I F (100) + I F (002) + I F (101) + I F (102) + I F (110) + I F (103)} a bottom peak ratio O F,
    Orientation degree of (002) plane in the inner region: I C (002) / {I C (100) + I C (002) + I C (101) + I C (102) + I C (110) + I C (103)} when the the bottom peak ratio O C,
    The ratio of the bottom peak ratio O F of the surface region relative to the bottom surface peak ratio O c of the internal region: O F / O c satisfies the 1.05 <O F / O c.
  2.  前記表面領域の平均結晶粒径をDF、前記内部領域の平均結晶粒径をDcとするとき、前記表面領域の平均結晶粒径DFに対する前記内部領域の平均結晶粒径Dcの比率:Dc/DFが、1.5<Dc/DFを満たすことを特徴とする請求項1に記載のマグネシウム合金材。 The average crystal grain diameter D F of the surface region, when the average crystal grain size of the inner region and D c, the ratio of the average crystal grain size D c of the inner region to the average grain diameter D F of the surface area 2. The magnesium alloy material according to claim 1, wherein: D c / D F satisfies 1.5 <D c / D F.
  3.  前記表面領域のビッカース硬度(Hv)をHF、前記内部領域のビッカース硬度(Hv)をHcとするとき、前記表面領域のビッカース硬度HFに対する前記内部領域のビッカース硬度Hcの比率:Hc/HFが、Hc/HF<0.85を満たすことを特徴とする請求項1又は2に記載のマグネシウム合金材。 Vickers hardness (Hv) H F of the surface region, wherein the Vickers hardness of the inner region (Hv) when the H c, the ratio of the Vickers hardness H c of the inner region with respect to the Vickers hardness H F of the surface area: H c / H F is a magnesium alloy material according to claim 1 or 2, characterized in that satisfy H c / H F <0.85.
  4.  前記マグネシウム合金は、添加元素にAlを5.0質量%以上12質量%以下含有することを特徴とする請求項1~3のいずれか1項に記載のマグネシウム合金材。 4. The magnesium alloy material according to claim 1, wherein the magnesium alloy contains 5.0% by mass to 12% by mass of Al as an additive element.
  5.  マグネシウム合金からなる素材に圧延を施してマグネシウム合金材を製造するマグネシウム合金材の製造方法であって、
     溶解したマグネシウム合金を双ロール鋳造法により連続鋳造した板状の素材を準備する準備工程と、
     前記素材に複数パスの圧延を施して、厚さ1.5mm以上の板状のマグネシウム合金材を製造する圧延工程とを具え、
     前記各パスの圧下率をいずれも25%以下とすることを特徴とするマグネシウム合金材の製造方法。
    A method for producing a magnesium alloy material by rolling a material made of a magnesium alloy to produce a magnesium alloy material,
    A preparation step of preparing a plate-like material continuously cast from a melted magnesium alloy by a twin roll casting method;
    A rolling process for producing a plate-like magnesium alloy material having a thickness of 1.5 mm or more by rolling a plurality of passes on the material,
    A method for producing a magnesium alloy material, wherein the rolling reduction of each pass is 25% or less.
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JP5757105B2 (en) 2015-07-29
WO2012115191A9 (en) 2012-12-27
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CN103380223B (en) 2016-05-04
TW201302334A (en) 2013-01-16

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