以下，對本發明進行詳細說明，但本發明並非限定於以下說明之實施形態。再者，若無特別說明，則有關數值A及B之記法「A～B」表示「A以上且B以下」之含義。相關記法中，於僅對數值B添加單位之情形時，該單位亦適用於數值A。 本發明之電氣音響轉換器用振動板邊緣材包含聚醯胺樹脂(A)作為主成分，根據需要進而包含非晶性聚醯胺樹脂(B)。此處，「主成分」表示電氣音響轉換器用振動板邊緣材中所含之聚醯胺樹脂(A)之比率超過50質量%。電氣音響轉換器用振動板邊緣材中所含之聚醯胺樹脂(A)之比率重要的是超過50質量%，較佳為60質量%以上，更佳為65質量%以上，進而較佳為70質量%以上。 [聚醯胺樹脂(A)] 本發明所用之聚醯胺樹脂(A)係以對苯二甲酸與脂肪族二胺為主成分聚合而得之半芳香族聚醯胺樹脂。 構成聚醯胺樹脂(A)之二羧酸成分(a-1)重要的是以對苯二甲酸作為主成分。即，重要的是二羧酸成分(a-1)中超過50莫耳%之成分為對苯二甲酸，更佳為60莫耳%以上，進而較佳為80莫耳%以上，尤佳為90莫耳%以上，尤其較佳為二羧酸成分(a-1)全體(100莫耳%)為對苯二甲酸。二羧酸成分(a-1)以對苯二甲酸作為主成分，藉此本發明之電氣音響轉換器用振動板邊緣材於耐熱性、加工性及低吸水性方面優異。再者，作為對苯二甲酸以外之二羧酸成分，可例示自間苯二甲酸或脂肪族羧酸、羥基羧酸衍生之二羧酸成分等。 構成聚醯胺樹脂(A)之二胺成分(a-2)重要的是以脂肪族二胺作為主成分。即，重要的是二胺成分(a-2)中超過50莫耳%之成分為脂肪族二胺，更佳為60莫耳%以上，進而較佳為80莫耳%以上，尤佳為90莫耳%以上，尤其較佳為二胺成分(a-2)全體(100莫耳%)為脂肪族二胺。本發明之電氣音響轉換器用振動板於耐熱性、低吸水性、成形性及加工性方面優異。再者，作為二胺成分(a-2)所含之除脂肪族二胺以外之成分，可列舉苯二甲胺等芳香族二胺成分。 上述脂肪族二胺成分只要為烷基鏈之兩末端具有胺基之二胺成分則並無特別限制，作為具體例，可列舉：1,2-乙二胺、1,3-丙二胺、1,4-丁二胺、1,5-戊二胺、1,6-己二胺、1,7-庚二胺、1,8-辛二胺、2-甲基-1,8-辛二胺、1,9-壬二胺、1,10-癸二胺、1,11-十一烷二胺、1,12-十二烷二胺等。 於該等中，就耐熱性或低吸水性與成形性、與加工性之均衡性優異之方面而言，較佳為以50質量%以上且100質量%以下之比率包含1,9-壬二胺，更佳為以60質量%以上且95質量%以下之比率包含，進而較佳為以70質量%以上且90質量%以下之比率包含。 又，就進一步賦予成形性或加工性之觀點而言，較佳為以1質量%以上且50質量%以下之比率包含2-甲基-1,8-辛二胺，更佳為以5質量%以上且40質量%以下之比率包含，進而較佳為以10質量%以上且30質量%以下之比率包含。 聚醯胺樹脂(A)之結晶熔解溫度較佳為260℃以上且340℃以下，更佳為270℃以上且335℃以下，進而較佳為280℃以上且330℃以下。若聚醯胺樹脂(A)之結晶熔解溫度為260℃以上，則電氣音響轉換器用振動板邊緣材之耐熱性提高。例如可賦予能夠耐受波峰溫度為260℃之回焊步驟之耐熱性。另一方面，若結晶熔解溫度為340℃以下，則例如於用於本發明之電氣音響轉換器用振動板邊緣材之膜之熔融成形中，使用通用之設備即可於相對低溫下進行加工，因此較佳。 [非晶性聚醯胺樹脂(B)] 本發明之電氣音響轉換器用振動板邊緣材除了聚醯胺樹脂(A)以外，根據需要亦可包含非晶性聚醯胺樹脂(B)。藉由進而包含非晶性聚醯胺樹脂(B)，可提高成形性，又，於非晶性聚醯胺樹脂(B)之玻璃轉移溫度高於聚醯胺樹脂(A)之情形時，可提高玻璃轉移溫度。再者，於本發明中，非晶性聚醯胺樹脂(B)係指結晶熔解焓未達5 J/g之聚醯胺樹脂。 作為構成非晶性聚醯胺樹脂(B)之酸成分，可例示：對苯二甲酸、間苯二甲酸、鄰苯二甲酸等芳香族二羧酸成分，草酸、丙二酸、琥珀酸、戊二酸、己二酸、庚二酸、辛二酸、壬二酸、癸二酸(sebacic acid)、癸二酸(decanedioic acid)、十二烷二酸、十四烷二羧酸等脂肪族二羧酸成分，自羥基羧酸衍生之二羧酸成分，脂環族二羧酸成分等。 作為構成非晶性聚醯胺樹脂(B)之二胺成分，可例示：1,2-乙二胺、1,3-丙二胺、1,4-丁二胺、1,5-戊二胺、1,6-己二胺、1,7-庚二胺、1,8-辛二胺、2-甲基-1,8-辛二胺、1,9-壬二胺、1,10-癸二胺、1,11-十一烷二胺、1,12-十二烷二胺、1,13-十三烷二胺、1,14-十四烷二胺、1,15-十五烷二胺、1,16-十六烷二胺、1,17-十七烷二胺、1,18-十八烷二胺、1,19-十九烷二胺、1,20-二十烷二胺等脂肪族二胺成分，4,4'-亞甲基雙(環己胺)(PACM)、4,4'-亞甲基雙(2-甲基環己胺)(MACM)等脂環族二胺成分，苯二胺、鄰苯二胺、間苯二胺、對苯二胺、鄰苯二甲胺、間苯二甲胺、對苯二甲胺等芳香族二胺成分等。 非晶性聚醯胺樹脂(B)除了包含上述二羧酸成分與上述二胺成分之聚醯胺成分以外，亦可包含內醯胺成分作為共聚合成分。具體而言，可例示：γ-丁內醯胺、ε-己內醯胺、ω-庚內醯胺、ω-己內醯胺、ω-十二內醯胺等。 非晶性聚醯胺樹脂(B)只要包含上述成分且結晶熔解焓未達5 J/g，則無特別限制，較佳為包含4,4'-亞甲基雙(環己胺)(PACM)及4,4'-亞甲基雙(2-甲基環己胺)(MACM)中任一者或兩者作為二胺成分。藉由非晶性聚醯胺樹脂(B)包含PACM及MACM中任一者或兩者作為二胺成分，可提高非晶性聚醯胺樹脂(B)之玻璃轉移溫度，進而於與聚醯胺樹脂(A)混合時可不損害耐熱性而賦予成形性。 於包含非晶性聚醯胺樹脂(B)之情形時，聚醯胺樹脂(A)與非晶性聚醯胺樹脂(B)之含有比率較佳為(A)：(B)＝99：1～60：40質量%之範圍，更佳為98：2～65：35質量%之範圍，進而較佳為97：3～70：30質量%之範圍。若聚醯胺樹脂(A)與非晶性聚醯胺樹脂(B)之含有比率於該範圍內，則可於維持聚醯胺樹脂(A)之結晶性及加工性之情況下賦予成形性。 電氣音響轉換器用振動板邊緣材之玻璃轉移溫度(Tg)較佳為120℃以上，更佳為130℃以上，進而較佳為140℃以上。若電氣音響轉換器用振動板邊緣材之玻璃轉移溫度為120℃以上，則可不損害耐熱性而賦予成形性。 電氣音響轉換器用振動板邊緣材之結晶熔解焓(ΔHm)較佳為30 J/g以上，更佳為40 J/g以上，進而較佳為50 J/g以上。若結晶熔解焓(ΔHm)為40 J/g以上，則可獲得結晶性較高之膜或成形品，進而電氣音響轉換器用振動板之耐熱性優異，因此較佳。 電氣音響轉換器用振動板邊緣材之結晶熔解溫度較佳為260℃以上且340℃以下，更佳為270℃以上且335℃以下，進而較佳為280℃以上且330℃以下。若電氣音響轉換器用振動板邊緣材之結晶熔解溫度為260℃以上，則可賦予充分之耐熱性。另一方面，若電氣音響轉換器用振動板邊緣材之結晶熔解溫度為340℃以下，則熔融成形時之成形性優異。 於本發明中，聚醯胺樹脂(A)與非晶性聚醯胺樹脂(B)之混合物之玻璃轉移溫度較佳為單一。所謂玻璃轉移溫度單一係表示對於混合物，於應變0.1%、頻率10 Hz、升溫速度3℃/min下藉由動態黏彈性之溫度分散測定(JIS K7198A法之動態黏彈性測定)測得之損耗正切(tanδ)之主分散之波峰存在一個，換言之，損耗正切(tanδ)之極大值存在一個。一般而言，聚合物摻合組合物之玻璃轉移溫度單一係表示進行混合之樹脂處於分子級相溶之狀態，可認定為相溶系。相反地，於摻合後損耗正切(tanδ)之主分散之波峰存在兩個之情形時，可謂非相溶系。一般而言，於非相溶系之情形時，施加有拉伸或彎曲等外力時會發生界面剝離而引起機械特性降低。藉由聚醯胺(A)與非晶性聚醯胺(B)為相溶系而可實現優異之加工性及成形性。 [電氣音響轉換器用振動板] 本發明之電氣音響轉換器用振動板邊緣材能夠應用於揚聲器或聽筒、麥克風、耳機等只要為電氣音響轉換器之各者，尤其可較佳地用作行動電話等之微揚聲器振動板。本發明之電氣音響轉換器用振動板邊緣材可藉由使用下述方法對具備以下所示之較佳特性之膜進行加工而獲得。 本發明之電氣音響轉換器用振動板邊緣材所用之膜較佳為依據JIS K7127之拉伸彈性模數為1000 MPa以上且未達2500 MPa。若拉伸彈性模數為1000 MPa以上，則不僅確保高溫域之播放性，且具有對用作電氣音響轉換器用振動板邊緣材而言充分之剛性(韌性)。就該觀點而言，拉伸彈性模數進而較佳為1500 MPa以上，尤佳為1800 MPa以上。另一方面，若拉伸彈性模數未達2500 MPa，則例如於微揚聲器之振動板之情形時，即便使用處理性或高輸出時之耐久性等優異之厚度20～40 μm之膜，最低共振頻率(f0：F-ZERO)亦充分低，確保低音域之播放性，音質良好，因此較佳。就該觀點而言，彈性模數進而較佳為2400 MPa以下，尤佳為2300 MPa以下。 本發明之電氣音響轉換器用振動板邊緣材所用之膜較佳為依據JIS P8115之耐折強度為1000次以上，更佳為1500次以上。若耐折強度於該範圍內，則高輸出時之耐久性優異，振動板不易產生龜裂或破損等。 本發明之電氣音響轉換器用振動板邊緣材所用之膜較佳為依據JIS K7127之拉伸斷裂伸長率為100%以上，更佳為200%以上。若拉伸斷裂伸長率於該範圍內，則不會產生破斷等故障，於各種形狀、例如需要深可拉性之形狀時亦可穩定加工。 進而，除上述成分以外，亦可於不超出本發明之要旨之範圍內對本發明之電氣音響轉換器用振動板邊緣材所用之膜適當調配其他樹脂或填充材、各種添加劑，例如熱穩定劑、紫外線吸收劑、光穩定劑、成核劑、著色劑、潤滑劑、阻燃劑等。 作為本發明之電氣音響轉換器用振動板邊緣材所用之膜之製膜方法，可採用公知方法，例如使用T型模頭之擠出澆鑄法或壓延法、或流延法等，並無特別限定，但就膜之生產性等方面而言，適合採用使用T型模頭之擠出澆鑄法。使用T型模頭之擠出澆鑄法時之成形溫度係根據所使用之組合物之流動特性或製膜性等而適當調整，大概為280℃以上且350℃以下。熔融混練可使用通常所用之單軸擠出機、雙軸擠出機、捏合機或攪拌器等，並無特別限定，但就混合樹脂組合物之均勻分散性、所得之膜之各特性之穩定性而言，更佳為使用雙軸擠出機、尤其是同向雙軸擠出機。 於使用T型模頭之擠出澆鑄法之情形時，所得之膜可快速冷卻而於非晶狀態下收取，亦可利用流延輥進行加熱或於非晶狀態下收取後實施加熱處理，而於結晶化狀態下收取。一般而言，非晶狀態之膜其耐久性或加工性優異，結晶化後之膜其耐熱性或剛性(韌性)優異，因此重要的是根據用途而使用最合適之結晶狀態之膜。 本發明之電氣音響轉換器用振動板邊緣材所用之膜之厚度並無特別限定，作為電氣音響轉換器用振動板邊緣材，通常為1～200 μm。又，製膜時亦重要的是儘可能減小膜於自擠出機之行進方向(MD)與其正交方向(TD)上之物性之各向異性。 如此所得之膜經過進一步加工而用作電氣音響轉換器用振動板邊緣材。加工方法並無特別限定，例如於揚聲器振動板之情形時，考慮其玻璃轉移溫度或軟化溫度而對該膜進行加熱，藉由加壓成形或真空成形等將至少一部分加工成圓頂形或錐形等而使用。又，振動板於俯視下之形狀為任意，並無特別限制，可選擇圓形、楕圓形、卵形等。 圖1係表示本發明之一實施形態之微揚聲器振動板1之結構之圖，為將俯視下呈圓形之微揚聲器振動板1沿通過圓之中心線之面切斷後所得之剖視圖。如圖1所示，微揚聲器振動板1以加工成圓頂形之圓頂部(主體)1a為中心，具有安裝於音圈2之凹嵌部1b、周緣部(邊緣)1c，且其外周具有貼附於框架等之外部貼附部1d。圖2係表示本發明之另一實施形態之微揚聲器振動板11之結構之圖，與圖1相對應。如圖2所示，微揚聲器振動板11安裝於音圈2上所安裝之圓頂形高彈性體12之周圍，具有俯視下呈環形之高彈性體貼附部11i、加工成錐形之錐形部11j，且其外周具有周緣部(邊緣)11c。圖3係表示本發明之進而另一實施形態之微揚聲器振動板21之結構之圖，與圖1相對應。如圖3所示，微揚聲器振動板21以加工成圓頂形之圓頂部(主體)21a為中心，具有安裝於音圈2之凹嵌部21b、加工成錐形之錐形部21j、及周緣部(邊緣)21c。如微揚聲器振動板21所示，本發明之電氣音響轉換器用振動板邊緣材其一部分可被加工成圓頂形，且除該部分以外之其他一部分可被加工成錐形。再者，微揚聲器振動板11、21分別可將周緣部11c、21c直接安裝於框架等，亦可經由其他構件而安裝於框架等。 本發明之電氣音響轉換器用振動板邊緣材所用之膜由於拉伸彈性模數不會過高，故而尤其於用於小型電氣音響轉換器用振動板邊緣材之情形時，確保低音域之播放性，音質良好，因此較佳。此處，作為振動板之大小，適宜採用如下：最大徑為25 mm以下、較佳為20 mm以下，下限通常為5 mm左右。再者，關於最大徑，於振動板之形狀為圓形之情形時採用直徑，於楕圓形或卵形之情形時採用長徑。 可對振動板面適當賦予所謂相切邊(tangential edge)之橫截面形狀為V字形之槽等。圖4表示本發明之另一實施形態之微揚聲器振動板1'之俯視圖。微揚聲器振動板1'於圓形之圓頂部(主體)1a'之外周緣部具有賦予有複數個相切邊1e之相切邊部1g、及賦予有複數個相切邊1f之相切邊部1h。於具有相切邊之形態中，若膜之平均厚度較佳為3～40 μm、更佳為5～38 μm，則充分確保厚度，因此處理性亦良好，加壓成形等單位時間之加工性或加工精度(形狀之再現性)容易提高，因此較佳。 又，本發明之電氣音響轉換器用振動板邊緣材亦可為積層體，其於正面層及背面層具有該電氣音響轉換器用振動板邊緣材，於中間層具有至少一層阻尼效應(內部損耗)較高之黏著層。圖5表示本發明之一實施形態之作為積層體之電氣音響轉換器用振動板邊緣材10。作為積層體之電氣音響轉換器用振動板邊緣材10於正面層及背面層具有單層之電氣音響轉換器用振動板邊緣材3，於中間層具有一層黏著劑層4。藉由設為此種積層結構，不僅可賦予正面層及背面層之電氣音響轉換器用振動板邊緣材所具有之耐熱性、剛性、耐久性及成形性，且可賦予中間層所具有之優異之衰減特性。作為積層體之電氣音響轉換器用振動板邊緣材之製作方法並無特別限制。例如可列舉如下方法等：對具有上述較佳特性之一對膜進行加工而分別製作構成正面層及背面層之電氣音響轉換器用振動板邊緣材，將該等經由用於中間層之黏著劑進行接著而製作；或者將具有上述較佳特性之一對膜經由用於中間層之黏著劑進行接著而製作積層膜，利用上述方法對該積層膜進行加工。於該情形時，作為用於中間層之黏著劑之種類，可列舉：丙烯酸系黏著劑、橡膠系黏著劑、聚矽氧系黏著劑、胺基甲酸酯系黏著劑等，就接著性之觀點而言，較佳為使用丙烯酸系或聚矽氧系黏著劑。又，於該情形時，正面層及背面層之厚度分別較佳為1 μm以上且30 μm以下，更佳為2 μm以上且25 μm以下，進而較佳為3 μm以上且20 μm以下。另一方面，中間層厚度較佳為3 μm以上且50 μm以下，更佳為5 μm以上且40 μm以下，進而較佳為10 μm以上且30 μm以下。若中間層之材料種類或各層厚度為該構成，則可獲得於維持各種機械特性或成形之情況下衰減特性亦優異之振動板。 進而，為了振動板之加工適應性或防塵性、或音響特性調整或設計性提高等，可進而適當對本發明之電氣音響轉換器用振動板邊緣材所用之膜或所成形之振動板之表面進行塗佈或積層抗靜電劑或各種彈性體(例如胺基甲酸酯系、聚矽氧系、烴系、氟系等)、或者蒸鍍金屬、或者濺鍍或著色(黑色或白色等)等之處理。進而，亦可適當進行與鋁等金屬或其他膜之積層、或與不織布之複合化等。 本發明之電氣音響轉換器用振動板邊緣材於用於揚聲器振動板之情形時，高輸出時之耐久性優異。例如於行動電話中，相對於通用機型之0.3 W左右，能夠應對可適用於高輸出機型之0.6～1.0 W左右之耐輸出量。又，含有聚醯胺樹脂(A)作為主成分之膜不僅作為揚聲器振動板、尤其微揚聲器之振動板之基本音響特性優異，且耐熱性或振動板加工時之成形性亦優異。 再者，一般而言，所謂「膜」係指與長度及寬度相比厚度極小、且最大厚度被任意限定之薄平製品，通常指以輥形供給者(JIS K6900)，一般而言，所謂「片材」，根據JIS之定義係指較薄、其厚度相對小於長度與寬度之扁平製品。但片材與膜之界限並不明確，本發明中無需於表述上區別兩者，因此於本發明中，於稱為「膜」之情形時亦包括「片材」，於稱為「片材」之情形時亦包括「膜」。 [實施例] 以下利用實施例進行更詳細之說明，但本發明並不受該等之任何限制。再者，針對本說明書中記載之原料及本發明之電氣音響轉換器用振動板邊緣材所用之膜的各種測定係藉由如下方式進行。 (1)玻璃轉移溫度、結晶熔解溫度、結晶熔解焓 針對各種原料及所得之膜，依據JIS K7121以加熱速度10℃/min進行示差掃描熱量計(DSC)測定，測定升溫過程中之玻璃轉移溫度、結晶熔解溫度及結晶熔解焓。 (2)拉伸彈性模數 針對所得之膜，依據JIS K7127於溫度23℃之條件下進行測定。 (3)耐折強度 針對所得之膜，依據JIS P8115於溫度23℃之條件下進行測定。 (4)拉伸斷裂伸長率 針對所得之膜，依據JIS K7127於溫度23℃、試驗速度200 mm/min之條件下進行測定。 1.聚醯胺樹脂(A) (A)-1：PA9T/2-Me8T(KURARAY股份有限公司製造，商品名：Genestar N1000A，對苯二甲酸/1,9-壬二胺/2-甲基-1,8-辛二胺＝50/42.5/7.5莫耳%，結晶熔解溫度：302℃，結晶熔解焓：59 J/g，玻璃轉移溫度：120℃) (A)-2：PA9T/2-Me8T(KURARAY股份有限公司製造，商品名：Genestar N1001D，對苯二甲酸/1,9-壬二胺/2-甲基-1,8-辛二胺＝50/25/25莫耳%，結晶熔解溫度：266℃，結晶熔解焓：46 J/g，玻璃轉移溫度：120℃) 2.非晶性聚醯胺樹脂(B) (B)-1：MACMT/MACMI/12(EMS股份有限公司製造，商品名：Grilamid TR60，對苯二甲酸/間苯二甲酸/MACM/ω-十二內醯胺＝22/17/37/24莫耳%，結晶熔解焓：0 J/g，玻璃轉移溫度：190℃) (實施例1) 使用Φ25 mm同向雙軸擠出機將作為聚醯胺樹脂(A)之(A)-1於320℃下進行混練後，自T型模頭擠出，繼而利用約100℃之流延輥進行快速冷卻，而製作厚度25 μm之膜。未進行結晶化處理。對所得之膜進行上述(1)～(4)之測定。結果如表1所示。 (實施例2) 將流延輥之溫度設為210℃，於結晶化狀態下收取膜，除此以外，藉由與實施例1相同之方法進行膜之製作及測定。結果如表1所示。 (實施例3) 將(A)-1與(B)-1以混合質量比90：10進行乾摻後使用，除此以外，藉由與實施例1相同之方法進行膜之製作及測定。結果如表1所示。再者，未進行結晶化處理。 (實施例4) 將(A)-1與(B)-1以混合質量比90：10進行乾摻後使用，將流延輥之溫度設為210℃，於結晶化狀態下收取膜，除此以外，藉由與實施例1相同之方法進行膜之製作及測定。結果如表1所示。 (實施例5) 將(A)-1與(B)-1以混合質量比80：20進行乾摻後使用，除此以外，藉由與實施例1相同之方法進行膜之製作及測定。結果如表1所示。再者，未進行結晶化處理。 (實施例6) 將(A)-1與(B)-1以混合質量比70：30進行乾摻後使用，除此以外，藉由與實施例1相同之方法進行膜之製作及測定。結果如表1所示。再者，未進行結晶化處理。 (實施例7) 將(A)-1與(B)-1以混合質量比60：40進行乾摻後使用，除此以外，藉由與實施例1相同之方法進行膜之製作及測定。結果如表1所示。再者，未進行結晶化處理。 (實施例8) 使用(A)-2作為原料，除此以外，藉由與實施例1相同之方法進行膜之製作及測定。結果如表1所示。再者，未進行結晶化處理。 (比較例1) 將(A)-1與(B)-1以混合質量比50：50進行乾摻後使用，除此以外，藉由與實施例1相同之方法進行膜之製作及測定。結果如表1所示。再者，未進行結晶化處理。 (比較例2) 使用(N)-1：PES(住友化學股份有限公司製造，商品名：Sumikaexcel 4800G，聚醚碸，玻璃轉移溫度：225℃)作為原料，將混練溫度設為350℃，將流延輥溫度設為200℃，除此以外，藉由與實施例1相同之方法進行膜之製作及測定。結果如表1所示。再者，未進行結晶化處理。 (比較例3) 使用(N)-2：PEEK(DAICEL EVONIK股份有限公司製造，Vestakeep 3300G，結晶熔解溫度：334℃，結晶熔解焓：29 J/g，玻璃轉移溫度：143℃)作為原料，將混練溫度設為380℃，流延輥溫度設為230℃，於結晶化狀態下收取膜，除此以外，藉由與實施例1相同之方法進行膜之製作及測定。結果如表1所示。 (比較例4) 使用(N)-3：PPSU(SOLVAY SPECIALTY POLYMERS股份有限公司製造，商品名：Radel R-5000，聚苯碸，玻璃轉移溫度：220℃)作為原料，將混練溫度設為350℃，將流延輥溫度設為200℃，除此以外，藉由與實施例1相同之方法進行膜之製作及測定。結果如表1所示。再者，未進行結晶化處理。 (比較例5) 將(N)-2與(N)-3以混合質量比50：50進行乾摻後用作原料，將混練溫度設為380℃，除此以外，藉由與實施例1相同之方法進行膜之製作及測定。結果如表1所示。再者，未進行結晶化處理。 (比較例6) 使用(N)-2作為原料，將混練溫度設為380℃，除此以外，藉由與實施例1相同之方法進行膜之製作及測定。結果如表1所示。再者，未進行結晶化處理。 [表1]
於實施例1中，於非晶狀態下使用以本發明之聚醯胺樹脂(A)為主成分之膜。該膜由於拉伸彈性模數處於適當範圍內，故而剛性(韌性)進而處理性優異，低音域之播放性亦優異。 於實施例2中，對以本發明之聚醯胺樹脂(A)為主成分之膜實施熱處理，而於結晶化狀態下使用。可知該膜雖然耐久性及加工性稍遜於非晶狀態之膜，但維持對用作振動板而言充分之特性，且剛性特別優異。 於實施例3、5～7中，於非晶狀態下使用以本發明之聚醯胺樹脂(A)與非晶性聚醯胺樹脂(B)之混合物為主成分之膜。可知該膜由於聚醯胺樹脂(A)與非晶性聚醯胺樹脂(B)為相溶系，且非晶性聚醯胺樹脂(B)之玻璃轉移溫度高於聚醯胺樹脂(A)，故而於維持各種特性之情況下玻璃轉移溫度提高。 於實施例4中，對以本發明之聚醯胺樹脂(A)與非晶性聚醯胺樹脂(B)之混合物為主成分之膜實施熱處理，而於結晶化狀態下使用。可知該膜雖然耐久性及加工性稍遜於非晶狀態之膜，但維持對用作振動板而言充分之特性，且剛性特別優異。 於實施例8中，於非晶狀態下使用以共聚合成分(2-甲基-1,8-辛二胺)之比率高於實施例1中使用之原料(PA9T)之原料為主成分之膜。可知該膜雖然結晶熔解焓及結晶熔解溫度低於實施例1之膜，但具有對用作振動板而言充分之耐熱性，且其他各種特性為同等水平。 另一方面，於比較例1中，於非晶狀態下使用以本發明之聚醯胺樹脂(A)與非晶性聚醯胺樹脂(B)之混合物為主成分之膜。該膜由於非晶性聚醯胺樹脂(B)於混合物中所占之比率過高，故而結晶熔解焓較低、即結晶性降低，耐熱性不充分。 於比較例2中，使用以作為耐熱性非晶性樹脂之PES(聚醚碸)為主成分之膜。該膜由於使用非晶性樹脂，故而無熔點，耐熱性較差。又，不僅拉伸彈性模數較高、低音之播放性較差，且拉伸斷裂伸長率較低，因此加工性、尤其深拉拔成形性亦不充分。 於比較例3中，對以PEEK(聚醚醚酮)為主成分之膜實施熱處理，而於結晶化狀態下使用。該膜不僅拉伸彈性模數較高，低音之播放性較差，且高輸出時之耐久性亦不充分。 於比較例4中，使用以作為耐熱性非晶性樹脂之PPSU(聚苯碸)為主成分之膜。該膜由於使用非晶性樹脂，故而無熔點，耐熱性較差。又，耐折強度較低，耐出力時之耐久性不充分。 於比較例5中，於非晶狀態下使用將PEEK與PPSU以50：50質量%混合之膜。該膜由於PEEK與PPSU為非相溶系或部分相溶系，故而確認到兩個玻璃轉移溫度。非晶性樹脂成分之比率較高，結晶熔解焓較低、即結晶性降低，耐熱性不充分。 於比較例6中，於非晶狀態下使用以PEEK為主成分之膜。拉伸彈性模數略高，但大致處於較佳範圍內，整體特性之均衡性優異。Hereinafter, the present invention will be described in detail, but the present invention is not limited to the embodiments described below. In addition, unless otherwise indicated, the notation "A to B" of the numerical values A and B means "A or more and B or less". In the related notation, the unit also applies to the value A when only the unit of the value B is added. The vibrating plate edge material for an electroacoustic transducer according to the present invention contains a polyamide resin (A) as a main component and, if necessary, an amorphous polyamine resin (B). Here, the "main component" indicates that the ratio of the polyamide resin (A) contained in the vibrating plate edge material for the electroacoustic transducer exceeds 50% by mass. The ratio of the polyamide resin (A) contained in the vibrating plate edge material for the electroacoustic transducer is preferably more than 50% by mass, preferably 60% by mass or more, more preferably 65% by mass or more, and still more preferably 70% by mass. More than % by mass. [Polyurethane Resin (A)] The polyamidamide resin (A) used in the present invention is a semi-aromatic polyamide resin obtained by polymerizing terephthalic acid and an aliphatic diamine as a main component. The dicarboxylic acid component (a-1) constituting the polyamide resin (A) is important as terephthalic acid as a main component. That is, it is important that the component exceeding 50 mol% in the dicarboxylic acid component (a-1) is terephthalic acid, more preferably 60 mol% or more, still more preferably 80 mol% or more, and particularly preferably 90 mol% or more, and particularly preferably the dicarboxylic acid component (a-1) as a whole (100 mol%) is terephthalic acid. In the dicarboxylic acid component (a-1), terephthalic acid is used as a main component, and the vibrating plate edge material for an electroacoustic transducer of the present invention is excellent in heat resistance, workability, and low water absorbability. In addition, examples of the dicarboxylic acid component other than terephthalic acid include dicarboxylic acid components derived from isophthalic acid or an aliphatic carboxylic acid or a hydroxycarboxylic acid. It is important that the diamine component (a-2) constituting the polyamide resin (A) is an aliphatic diamine as a main component. That is, it is important that the component of the diamine component (a-2) exceeding 50 mol% is an aliphatic diamine, more preferably 60 mol% or more, further preferably 80 mol% or more, and particularly preferably 90. More than or equal to mol%, particularly preferably the diamine component (a-2) as a whole (100 mol%) is an aliphatic diamine. The vibrating plate for an electroacoustic transducer of the present invention is excellent in heat resistance, low water absorbability, moldability, and workability. In addition, the component other than the aliphatic diamine contained in the diamine component (a-2) may, for example, be an aromatic diamine component such as xylylenediamine. The aliphatic diamine component is not particularly limited as long as it is an amine group having an amine group at both terminals of the alkyl chain, and specific examples thereof include 1,2-ethylenediamine and 1,3-propanediamine. 1,4-butanediamine, 1,5-pentanediamine, 1,6-hexanediamine, 1,7-heptanediamine, 1,8-octanediamine, 2-methyl-1,8-octyl Diamine, 1,9-nonanediamine, 1,10-decanediamine, 1,11-undecanediamine, 1,12-dodecanediamine, and the like. In the above, it is preferable that the heat resistance or the low water absorption property is excellent in the balance between the moldability and the workability, and the ratio of the content of 50% by mass or more and 100% by mass or less is preferably 1,9-壬2. The amine is more preferably contained in a ratio of 60% by mass or more and 95% by mass or less, and still more preferably 70% by mass or more and 90% by mass or less. In addition, from the viewpoint of further imparting formability and workability, it is preferred to contain 2-methyl-1,8-octanediamine in a ratio of 1% by mass or more and 50% by mass or less, more preferably 5 parts by mass. The ratio of % or more and 40% by mass or less is contained, and more preferably 10% by mass or more and 30% by mass or less. The crystal melting temperature of the polyamide resin (A) is preferably 260 ° C or more and 340 ° C or less, more preferably 270 ° C or more and 335 ° C or less, and still more preferably 280 ° C or more and 330 ° C or less. When the crystal melting temperature of the polyamide resin (A) is 260 ° C or higher, the heat resistance of the vibrating plate edge material for the electroacoustic transducer is improved. For example, heat resistance capable of withstanding a reflow step of a peak temperature of 260 ° C can be imparted. On the other hand, when the crystal melting temperature is 340 ° C or lower, for example, in the melt molding of the film for the vibrating plate edge material of the electroacoustic transducer of the present invention, it can be processed at a relatively low temperature by using a general-purpose apparatus. Preferably. [Amorphous Polyamide Resin (B)] The vibrating plate edge material for the electroacoustic transducer of the present invention may contain an amorphous polyamine resin (B) as needed in addition to the polyamide resin (A). When the amorphous polyamine resin (B) is further contained, the moldability can be improved, and when the glass transition temperature of the amorphous polyamide resin (B) is higher than that of the polyamide resin (A), Can increase the glass transfer temperature. Further, in the present invention, the amorphous polyamine resin (B) means a polyamidamide resin having a crystal melting enthalpy of less than 5 J/g. Examples of the acid component constituting the amorphous polyamine resin (B) include aromatic dicarboxylic acid components such as terephthalic acid, isophthalic acid, and phthalic acid, and oxalic acid, malonic acid, and succinic acid. Fatty acids such as glutaric acid, adipic acid, pimelic acid, suberic acid, azelaic acid, sebacic acid, decanedioic acid, dodecanedioic acid, tetradecanedicarboxylic acid A dicarboxylic acid component, a dicarboxylic acid component derived from a hydroxycarboxylic acid, an alicyclic dicarboxylic acid component or the like. Examples of the diamine component constituting the amorphous polyamine resin (B) include 1,2-ethanediamine, 1,3-propanediamine, 1,4-butanediamine, and 1,5-pentane. Amine, 1,6-hexanediamine, 1,7-heptanediamine, 1,8-octanediamine, 2-methyl-1,8-octanediamine, 1,9-nonanediamine, 1,10 -decanediamine, 1,11-undecanediamine, 1,12-dodecanediamine, 1,13-tridecanediamine, 1,14-tetradecanediamine, 1,15-ten Pentadecanediamine, 1,16-hexadecanediamine, 1,17-heptadecanediamine, 1,18-octadecanediamine, 1,19-nonadecanediamine, 1,20-di Aliphatic diamine component such as decaminane diamine, 4,4'-methylenebis(cyclohexylamine) (PACM), 4,4'-methylenebis(2-methylcyclohexylamine) (MACM) An alicyclic diamine component, an aromatic diamine component such as phenylenediamine, o-phenylenediamine, m-phenylenediamine, p-phenylenediamine, o-xylylenediamine, m-xylylenediamine or p-xylylenediamine Wait. The amorphous polyamine resin (B) may contain an indoleamine component as a copolymerization component in addition to the polycarboxylic acid component of the above dicarboxylic acid component and the above diamine component. Specifically, γ-butyrolactam, ε-caprolactam, ω-heptanoin, ω-caprolactam, ω-dodecanamide, and the like can be exemplified. The amorphous polyamine resin (B) is not particularly limited as long as it contains the above components and the crystal melting enthalpy is less than 5 J/g, and preferably contains 4,4'-methylenebis(cyclohexylamine) (PACM). And any one or both of 4,4'-methylenebis(2-methylcyclohexylamine) (MACM) as a diamine component. By using the amorphous polyamine resin (B) comprising either or both of PACM and MACM as the diamine component, the glass transition temperature of the amorphous polyamide resin (B) can be increased, and further When the amine resin (A) is mixed, moldability can be imparted without impairing heat resistance. In the case of the amorphous polyamine resin (B), the content ratio of the polyamide resin (A) to the amorphous polyamide resin (B) is preferably (A): (B) = 99: The range of 1 to 60: 40% by mass, more preferably 98:2 to 65:35 mass%, still more preferably 97:3 to 70:30% by mass. When the content ratio of the polyamide resin (A) to the amorphous polyimide resin (B) is within this range, moldability can be imparted while maintaining the crystallinity and processability of the polyamide resin (A). . The glass transition temperature (Tg) of the vibrating plate edge material for the electroacoustic transducer is preferably 120 ° C or more, more preferably 130 ° C or more, and still more preferably 140 ° C or more. When the glass transition temperature of the vibrating plate edge material for an electroacoustic transducer is 120 ° C or more, moldability can be imparted without impairing heat resistance. The crystal melting enthalpy (ΔHm) of the vibrating plate edge material for the electroacoustic transducer is preferably 30 J/g or more, more preferably 40 J/g or more, and still more preferably 50 J/g or more. When the crystal melting enthalpy (ΔHm) is 40 J/g or more, a film or a molded article having high crystallinity can be obtained, and the vibrating plate for an electroacoustic transducer is excellent in heat resistance. The crystal melting temperature of the vibrating plate edge material for the electroacoustic transducer is preferably 260 ° C or more and 340 ° C or less, more preferably 270 ° C or more and 335 ° C or less, and still more preferably 280 ° C or more and 330 ° C or less. When the crystal melting temperature of the vibrating plate edge material for the electroacoustic transducer is 260 ° C or higher, sufficient heat resistance can be imparted. On the other hand, when the crystal melting temperature of the vibrating plate edge material for the electroacoustic transducer is 340 ° C or lower, the moldability at the time of melt molding is excellent. In the present invention, the glass transition temperature of the mixture of the polyamide resin (A) and the amorphous polyamide resin (B) is preferably single. The so-called glass transition temperature alone means the loss tangent measured by the temperature dispersion measurement of dynamic viscoelasticity (dynamic viscoelasticity measurement by JIS K7198A method) at a strain of 0.1%, a frequency of 10 Hz, and a temperature increase rate of 3 ° C/min. There is one peak of the main dispersion of (tan δ), in other words, there is one maximum value of the loss tangent (tan δ). In general, the glass transition temperature of the polymer blend composition is a single state in which the resin to be mixed is in a state of being dissolved at a molecular level, and is considered to be a compatible system. Conversely, when there are two peaks of the main dispersion of the loss tangent (tan δ) after blending, it is an incompatible system. In general, in the case of an incompatible system, when an external force such as stretching or bending is applied, interfacial peeling occurs to cause deterioration of mechanical properties. Excellent processability and formability can be achieved by dissolving the polyamine (A) and the amorphous polyamine (B). [Vibration plate for electroacoustic transducer] The vibrating plate edge material for the electroacoustic transducer of the present invention can be applied to a speaker, an earpiece, a microphone, an earphone, etc., and can be preferably used as a mobile phone, etc., as long as it is an electric acoustic transducer. The micro-speaker vibrating plate. The vibrating plate edge material for an electroacoustic transducer of the present invention can be obtained by processing a film having the preferred characteristics shown below by using the following method. The film for the vibrating plate edge material for an electroacoustic transducer of the present invention preferably has a tensile modulus of elasticity of 1000 MPa or more and less than 2,500 MPa in accordance with JIS K7127. When the tensile elastic modulus is 1000 MPa or more, not only the high-performance range is ensured, but also the rigidity (toughness) sufficient for use as a vibrating plate edge material for an electroacoustic transducer is obtained. From this point of view, the tensile modulus of elasticity is further preferably 1,500 MPa or more, and particularly preferably 1800 MPa or more. On the other hand, when the tensile modulus is less than 2,500 MPa, for example, in the case of a vibrating plate of a microspeaker, a film having a thickness of 20 to 40 μm which is excellent in handleability or high output durability is used. The resonance frequency (f0: F-ZERO) is also sufficiently low to ensure the playability of the low range and the sound quality is good, so it is preferable. From this point of view, the elastic modulus is more preferably 2400 MPa or less, and particularly preferably 2300 MPa or less. The film for the vibrating plate edge material for an electroacoustic transducer of the present invention preferably has a folding strength of 1,000 or more, more preferably 1,500 or more, in accordance with JIS P8115. When the folding endurance strength is within this range, the durability at the time of high output is excellent, and the vibrating plate is less likely to be cracked or broken. The film for the vibrating plate edge material for an electroacoustic transducer of the present invention preferably has a tensile elongation at break of 100% or more, more preferably 200% or more, in accordance with JIS K7127. When the tensile elongation at break is within this range, failure such as breakage does not occur, and processing can be stably performed in various shapes such as a shape requiring deep drawability. Further, in addition to the above-described components, other resins or fillers, various additives such as heat stabilizers and ultraviolet rays may be appropriately blended to the film used for the vibrating plate edge material of the electroacoustic transducer of the present invention within the range not exceeding the gist of the present invention. Absorbents, light stabilizers, nucleating agents, colorants, lubricants, flame retardants, and the like. The film forming method of the film for the vibrating plate edge material of the electroacoustic transducer of the present invention can be carried out by a known method, for example, an extrusion casting method using a T-die, a calendering method, a casting method, or the like, and is not particularly limited. However, in terms of productivity of the film, etc., an extrusion casting method using a T-die is suitable. The molding temperature in the extrusion casting method using the T-die is appropriately adjusted depending on the flow characteristics, film forming properties, and the like of the composition to be used, and is approximately 280 ° C or more and 350 ° C or less. The melt-kneading can be carried out by using a uniaxial extruder, a twin-screw extruder, a kneader or a stirrer which are usually used, and is not particularly limited, but the uniform dispersibility of the mixed resin composition and the stability of each characteristic of the obtained film are obtained. In terms of properties, it is more preferred to use a twin-screw extruder, especially a co-rotating twin-screw extruder. In the case of the extrusion casting method using a T-die, the obtained film can be rapidly cooled and collected in an amorphous state, or can be heated by a casting roll or charged in an amorphous state, and then subjected to heat treatment, and It is collected in the state of crystallization. In general, a film in an amorphous state is excellent in durability and workability, and a film after crystallization is excellent in heat resistance or rigidity (toughness). Therefore, it is important to use a film of an optimum crystal state depending on the application. The thickness of the film used for the vibrating plate edge material for the electroacoustic transducer of the present invention is not particularly limited, and is usually 1 to 200 μm as the vibrating plate edge material for the electroacoustic transducer. Further, it is also important in film formation to minimize the anisotropy of the physical properties of the film in the traveling direction (MD) from the extruder and its orthogonal direction (TD). The film thus obtained was further processed to be used as a vibrating plate edge material for an electroacoustic transducer. The processing method is not particularly limited. For example, in the case of a speaker diaphragm, the film is heated in consideration of the glass transition temperature or the softening temperature, and at least a part is processed into a dome shape or a cone by press molding or vacuum forming. Shape and use. Further, the shape of the vibrating plate in a plan view is arbitrary, and is not particularly limited, and a circular shape, a circular shape, an oval shape, or the like can be selected. Fig. 1 is a cross-sectional view showing the structure of a microspeaker diaphragm 1 according to an embodiment of the present invention, which is obtained by cutting a microspeaker diaphragm 1 having a circular shape in plan view along a plane passing through a center line of a circle. As shown in FIG. 1, the microspeaker diaphragm 1 has a concave portion 1b and a peripheral portion (edge) 1c attached to the voice coil 2 centering on a dome portion (main body) 1a which is formed into a dome shape, and has an outer periphery thereof. Attached to the external attachment portion 1d of the frame or the like. Fig. 2 is a view showing the structure of a microspeaker diaphragm 11 according to another embodiment of the present invention, corresponding to Fig. 1. As shown in FIG. 2, the microspeaker vibrating plate 11 is mounted around the dome-shaped high elastic body 12 mounted on the voice coil 2, and has a high-elastic body attaching portion 11i which is annular in plan view and is tapered in a tapered shape. The portion 11j has a peripheral portion (edge) 11c on its outer circumference. Fig. 3 is a view showing the configuration of a microspeaker diaphragm 21 according to still another embodiment of the present invention, corresponding to Fig. 1. As shown in FIG. 3, the microspeaker vibrating plate 21 has a concave portion 21b attached to the voice coil 2, a tapered portion 21j processed into a tapered shape, and a conical portion (main body) 21a formed in a dome shape. Peripheral portion (edge) 21c. As shown in the microspeaker vibrating plate 21, a part of the vibrating plate edge material for the electroacoustic transducer of the present invention can be processed into a dome shape, and a part other than the portion can be processed into a taper shape. Further, the microspeaker diaphragms 11 and 21 may be attached to the frame or the like directly to the peripheral edge portions 11c and 21c, respectively, or may be attached to the frame or the like via other members. The film used for the vibrating plate edge material for the electroacoustic transducer of the present invention is not excessively high in tensile elastic modulus, and therefore, in the case of the vibrating plate edge material for a small electric acoustic transducer, the playability of the low range is ensured. Sound quality is good, so it is better. Here, as the size of the vibrating plate, the following is preferable: the maximum diameter is 25 mm or less, preferably 20 mm or less, and the lower limit is usually about 5 mm. Further, regarding the maximum diameter, the diameter is used when the shape of the vibrating plate is circular, and the long diameter is used in the case of a circular or oval shape. A groove having a V-shaped cross-sectional shape such as a tangential edge may be appropriately applied to the surface of the vibrating plate. Fig. 4 is a plan view showing a microspeaker diaphragm 1' according to another embodiment of the present invention. The microspeaker diaphragm 1' has a tangent edge portion 1g to which a plurality of tangent edges 1e are provided and a tangent edge to which a plurality of tangent edges 1f are provided on the outer peripheral portion of the circular dome portion (body) 1a'. Department 1h. In the form of the tangent edge, when the average thickness of the film is preferably from 3 to 40 μm, more preferably from 5 to 38 μm, the thickness is sufficiently ensured, so that the handleability is also good, and workability per unit time such as press molding is performed. It is preferable that the processing accuracy (reproducibility of the shape) is easily improved. Further, the vibrating plate edge material for an electroacoustic transducer according to the present invention may be a laminated body having the vibrating plate edge material for the electroacoustic transducer on the front layer and the back layer, and having at least one damping effect (internal loss) in the intermediate layer. High adhesion layer. Fig. 5 shows a vibrating plate edge member 10 for an electroacoustic transducer as a laminated body according to an embodiment of the present invention. The vibrating plate edge material 10 for an electroacoustic transducer as a laminated body has a single-layer vibrating plate edge material 3 for an electroacoustic transducer on the front layer and the back layer, and has an adhesive layer 4 in the intermediate layer. By providing such a laminated structure, it is possible to impart not only heat resistance, rigidity, durability, and moldability to the vibrating plate edge material of the electroacoustic transducer for the front layer and the back layer, but also to provide excellent properties of the intermediate layer. Attenuation characteristics. The method for producing the vibrating plate edge material for the electroacoustic transducer as the laminated body is not particularly limited. For example, a method of processing a film having one of the above-described preferred characteristics to produce a vibrating plate edge material for an electroacoustic transducer that constitutes a front layer and a back layer, and the like, and the like, may be used as an adhesive for an intermediate layer. Next, it is produced; or a film having one of the above preferred characteristics is passed through an adhesive for the intermediate layer to form a laminated film, and the laminated film is processed by the above method. In this case, examples of the type of the adhesive used for the intermediate layer include an acrylic adhesive, a rubber adhesive, a polyoxygen adhesive, and a urethane adhesive, and the like. From the viewpoint, it is preferred to use an acrylic or polyoxynoxy adhesive. Moreover, in this case, the thickness of the front layer and the back layer is preferably 1 μm or more and 30 μm or less, more preferably 2 μm or more and 25 μm or less, and still more preferably 3 μm or more and 20 μm or less. On the other hand, the thickness of the intermediate layer is preferably 3 μm or more and 50 μm or less, more preferably 5 μm or more and 40 μm or less, and still more preferably 10 μm or more and 30 μm or less. When the material type of the intermediate layer or the thickness of each layer is such a configuration, a vibrating plate excellent in attenuation characteristics even when various mechanical properties or molding are maintained can be obtained. Further, the film used for the vibrating plate edge material of the electroacoustic transducer of the present invention or the surface of the formed vibrating plate can be appropriately coated for the processing suitability and dustproofness of the vibrating plate, or the adjustment of the acoustic characteristics or the design improvement. Cloth or laminated antistatic agent or various elastomers (such as urethane, polyoxyl, hydrocarbon, fluorine, etc.), or vapor deposited metal, or sputtered or colored (black or white, etc.) deal with. Further, it is also possible to suitably laminate a metal such as aluminum or another film or a composite with a non-woven fabric. When the vibrating plate edge material for the electroacoustic transducer of the present invention is used for a speaker vibrating plate, the durability at the time of high output is excellent. For example, in a mobile phone, it is possible to cope with a output of about 0.6 to 1.0 W that can be applied to a high-output model with respect to a general-purpose model of about 0.3 W. Further, the film containing the polyamine resin (A) as a main component is excellent not only as a speaker vibrating plate but also as a vibrating plate of a microspeaker, and is excellent in heat resistance or moldability during processing of a vibrating plate. In addition, in general, the term "film" refers to a thin flat product having a very small thickness and a maximum thickness which is arbitrarily limited in thickness, and is generally referred to as a roll-shaped supplier (JIS K6900). "Sheet", as defined by JIS, refers to a flat article that is relatively thin and whose thickness is relatively less than the length and width. However, the boundary between the sheet and the film is not clear. In the present invention, it is not necessary to distinguish between the two. Therefore, in the present invention, the term "film" also includes "sheet", which is called "sheet". The case also includes "film". [Examples] Hereinafter, the examples will be described in more detail, but the present invention is not limited thereto. Further, various measurement systems for the raw materials described in the present specification and the film for the vibrating plate edge material of the electroacoustic transducer of the present invention are carried out as follows. (1) Glass transition temperature, crystal melting temperature, and crystal melting 焓 For various raw materials and the obtained film, a differential scanning calorimeter (DSC) was measured at a heating rate of 10 ° C/min according to JIS K7121, and the glass transition temperature during the temperature rise was measured. , crystal melting temperature and crystal melting enthalpy. (2) Tensile modulus of elasticity The obtained film was measured in accordance with JIS K7127 at a temperature of 23 °C. (3) Folding strength The film obtained was measured in accordance with JIS P8115 at a temperature of 23 °C. (4) Tensile elongation at break The film thus obtained was measured in accordance with JIS K7127 at a temperature of 23 ° C and a test speed of 200 mm / min. 1. Polyamide resin (A) (A)-1: PA9T/2-Me8T (manufactured by KURARAY Co., Ltd., trade name: Genestar N1000A, terephthalic acid/1,9-nonanediamine/2-methyl -1,8-octanediamine=50/42.5/7.5 mol%, crystal melting temperature: 302 ° C, crystal melting enthalpy: 59 J/g, glass transition temperature: 120 ° C) (A)-2: PA9T/2 -Me8T (manufactured by KURARAY Co., Ltd., trade name: Genestar N1001D, terephthalic acid/1,9-nonanediamine/2-methyl-1,8-octanediamine = 50/25/25 mol%, Crystallization melting temperature: 266 ° C, crystal melting enthalpy: 46 J / g, glass transition temperature: 120 ° C) 2. Amorphous polyamide resin (B) (B) - 1: MACMT / MACMI / 12 (EMS shares limited Made by the company, trade name: Grilamid TR60, terephthalic acid / isophthalic acid / MACM / ω - dodecylamine = 22 / 17 / 37 / 24 mole %, crystal melting 焓: 0 J / g, glass Transfer temperature: 190 ° C) (Example 1) After (A)-1 as a polyamide resin (A) was kneaded at 320 ° C using a Φ 25 mm co-rotating twin-screw extruder, it was extruded from a T-die. Then, it was rapidly cooled by a casting roll of about 100 ° C to form a film having a thickness of 25 μm. No crystallization treatment was performed. The obtained film (1) to (4) were measured. The results are shown in Table 1. (Example 2) A film was produced and measured in the same manner as in Example 1 except that the temperature of the casting roll was 210 ° C and the film was collected in the crystallization state. The results are shown in Table 1. (Example 3) A film was produced and measured in the same manner as in Example 1 except that (A)-1 and (B)-1 were dry-blended at a mixing mass ratio of 90:10. The results are shown in Table 1. Further, no crystallization treatment was performed. (Example 4) After (A)-1 and (B)-1 were dry-blended at a mixing mass ratio of 90:10, the temperature of the casting roll was set to 210 ° C, and the film was collected in the crystallization state, except The production and measurement of the film were carried out in the same manner as in Example 1 except for the above. The results are shown in Table 1. (Example 5) A film was produced and measured in the same manner as in Example 1 except that (A)-1 and (B)-1 were dry-mixed at a mixing mass ratio of 80:20. The results are shown in Table 1. Further, no crystallization treatment was performed. (Example 6) A film was produced and measured in the same manner as in Example 1 except that (A)-1 and (B)-1 were dry-blended at a mixing ratio of 70:30. The results are shown in Table 1. Further, no crystallization treatment was performed. (Example 7) A film was produced and measured in the same manner as in Example 1 except that (A)-1 and (B)-1 were dry-blended at a mixing ratio of 60:40. The results are shown in Table 1. Further, no crystallization treatment was performed. (Example 8) A film was produced and measured in the same manner as in Example 1 except that (A)-2 was used as a raw material. The results are shown in Table 1. Further, no crystallization treatment was performed. (Comparative Example 1) Film production and measurement were carried out in the same manner as in Example 1 except that (A)-1 and (B)-1 were dry-blended at a mixing ratio of 50:50. The results are shown in Table 1. Further, no crystallization treatment was performed. (Comparative Example 2) Using (N)-1: PES (manufactured by Sumitomo Chemical Co., Ltd., trade name: Sumikaexcel 4800G, polyether oxime, glass transition temperature: 225 ° C) as a raw material, the kneading temperature was 350 ° C, The production and measurement of the film were carried out in the same manner as in Example 1 except that the casting roll temperature was set to 200 °C. The results are shown in Table 1. Further, no crystallization treatment was performed. (Comparative Example 3) Using (N)-2: PEEK (manufactured by DAICEL EVONIK Co., Ltd., Vestakeep 3300G, crystal melting temperature: 334 ° C, crystal melting enthalpy: 29 J/g, glass transition temperature: 143 ° C) as a raw material, The film was produced and measured in the same manner as in Example 1 except that the kneading temperature was 380 ° C, the casting roll temperature was 230 ° C, and the film was collected in the crystallization state. The results are shown in Table 1. (Comparative Example 4) Using (N)-3:PPSU (manufactured by SOLVAY SPECIALTY POLYMERS Co., Ltd., trade name: Radel R-5000, polyphenyl hydrazine, glass transition temperature: 220 ° C) as a raw material, the kneading temperature was set to 350. The production and measurement of the film were carried out in the same manner as in Example 1 except that the casting roll temperature was changed to 200 °C. The results are shown in Table 1. Further, no crystallization treatment was performed. (Comparative Example 5) (N)-2 and (N)-3 were dry-blended at a mixing mass ratio of 50:50, and used as a raw material, and the kneading temperature was set to 380 ° C, and the same as Example 1 The production and measurement of the film were carried out in the same manner. The results are shown in Table 1. Further, no crystallization treatment was performed. (Comparative Example 6) Film production and measurement were carried out in the same manner as in Example 1 except that (N)-2 was used as a raw material and the kneading temperature was 380 °C. The results are shown in Table 1. Further, no crystallization treatment was performed. [Table 1] In Example 1, a film containing the polyamine resin (A) of the present invention as a main component was used in an amorphous state. Since the film has a tensile modulus of elasticity within an appropriate range, it is excellent in rigidity (toughness) and handleability, and is excellent in the playback property in the low range. In Example 2, the film containing the polyamine resin (A) of the present invention as a main component was subjected to heat treatment, and was used in a crystallized state. Although the film was inferior to the film in an amorphous state in durability and workability, it was found to have sufficient characteristics for use as a vibrating plate, and was particularly excellent in rigidity. In Examples 3 and 5 to 7, a film containing a mixture of the polyamide resin (A) of the present invention and the amorphous polyamide resin (B) as a main component was used in an amorphous state. It is understood that the film is compatible with the polyimide resin (A) and the amorphous polyamide resin (B), and the glass transition temperature of the amorphous polyamide resin (B) is higher than that of the polyamide resin (A). Therefore, the glass transition temperature is increased while maintaining various characteristics. In the fourth embodiment, a film containing a mixture of the polyamide resin (A) of the present invention and the amorphous polyamine resin (B) as a main component is subjected to heat treatment, and is used in a crystallized state. Although the film was inferior to the film in an amorphous state in durability and workability, it was found to have sufficient characteristics for use as a vibrating plate, and was particularly excellent in rigidity. In Example 8, a raw material having a ratio of a copolymerization component (2-methyl-1,8-octanediamine) higher than that of the raw material (PA9T) used in Example 1 was used in an amorphous state as a main component. membrane. It is understood that the film has a crystal melting temperature and a crystal melting temperature lower than that of the film of Example 1, but has sufficient heat resistance for use as a vibrating plate, and other various characteristics are equivalent. On the other hand, in Comparative Example 1, a film containing a mixture of the polyamide resin (A) of the present invention and the amorphous polyamide resin (B) as a main component was used in an amorphous state. Since the ratio of the amorphous polyamine resin (B) to the mixture is too high, the film has a low crystal melting enthalpy, that is, the crystallinity is lowered, and the heat resistance is insufficient. In Comparative Example 2, a film mainly composed of PES (polyether oxime) which is a heat-resistant amorphous resin was used. Since this film uses an amorphous resin, it has no melting point and is inferior in heat resistance. Further, not only the tensile modulus of elasticity is high, the playability of the bass is poor, and the tensile elongation at break is low, so workability, particularly deep draw formability, is also insufficient. In Comparative Example 3, a film containing PEEK (polyether ether ketone) as a main component was subjected to heat treatment, and was used in a crystallized state. The film has a high tensile modulus, a poor bass performance, and insufficient durability at high output. In Comparative Example 4, a film containing PPSU (polyphenyl hydrazine) as a heat-resistant amorphous resin as a main component was used. Since this film uses an amorphous resin, it has no melting point and is inferior in heat resistance. Moreover, the folding strength is low, and the durability at the time of the output is insufficient. In Comparative Example 5, a film in which PEEK and PPSU were mixed at 50:50% by mass was used in an amorphous state. Since the membrane was incompatible or partially compatible with PEEK and PPSU, two glass transition temperatures were confirmed. The ratio of the amorphous resin component is high, the crystal melting enthalpy is low, that is, the crystallinity is lowered, and the heat resistance is insufficient. In Comparative Example 6, a film containing PEEK as a main component was used in an amorphous state. The tensile modulus of elasticity is slightly higher, but is generally in a preferred range, and the balance of the overall characteristics is excellent.